Porosity, pore size distribution and in situ strength of concrete
土木工程材料(civilengineeringmaterials)

土木工程材料(civil engineering materials)Question: what are the effects of porosity, pore size and pore size on the properties of the material (such as strength, heat insulation, impermeability, frost resistance, corrosion resistance, water absorption, etc.)?.The larger the porosity of the material is, the lower the strength of the material is, the worse the impermeability and corrosion resistance are, and the stronger the water absorption is. The insulation property and frost resistance of the material are related to the pore structure of the material. The more content of the small hole and the non communicating hole, the better the thermal insulation property and the frost resistance of the material..Question: a multi-storey residential building interior plastering is lime mortar, after the delivery of the wall generally bulging cracking, try to analyze the reasons. What measures should be taken to prevent this from happening?.This phenomenon is due to the presence of burned lime, lime burned due to slow reaction, and the reaction time of the rapid expansion of the volume and release a lot of heat, so that the lime mortar wall bulging and cracking phenomenon after delivery. In order to avoid this phenomenon, lime should be used before Chen Fu..Question: the greater the porosity, the worse the frost resistance of the material?.The porosity of the material consists of two kinds of open poresand closed pores, and the porosity of the material is the sum of the open porosity and the closed porosity. The damage of the material due to freezing and thawing is mainly due to the freezing of water in the pores. The more water entering the pore, the worse the frost resistance of the material. Water is difficult to enter into the closed pores of materials. If the pores of the material are mainly closed pores, even if the porosity of the material is large, the moisture inside the material will not be much. In this case, the frost resistance of the material will not be poor..Question: why is slag cement, volcanic ash cement superior to Portland cement in corrosion resistance?.Because the hydration reaction of slag and calcium hydroxide volcano ash and clinker, C-S-H hydration products, the calcium hydroxide content in cement paste is greatly reduced, and the calcium hydroxide poor corrosion resistance. On the other hand, more hydrated products are formed, which makes the structure of cement stone more compact and improves the corrosion resistance of cement stone..Question: why is the dry shrinkage of fly ash cement smaller than that of pozzolanic cement?.The majority of fly ash are round particles with dense surface, while volcanic ash is irregular particles with porous surface. Generally speaking, when the cement paste reaches the same fluidity, the latter needs more water, which makes the hardened cement stone shrink more..Question: why shouldn't high alumina cement be cured at temperatures higher than 30?.In the process of high alumina cement hydration, when the temperature is below 20 DEG C, the main hydration products of CaOoAl2O3o10H2O, temperature 20 ~ 30 degrees, the main hydration products of 2CaOoAl2O3o8H2O, when the temperature is higher than 30 DEG C when the main hydration products3CaOoAl2O3o6H2O, the product of low strength, but not because of high alumina cement in the maintenance temperature higher than 30 DEG C under..Question: why is not the thinner the cement, the higher the strength must be?.Generally speaking, the fine particle of cement is beneficial to increase the hydration speed and sufficient hydration of cement, so that it is beneficial to the strength, especially the early strength. But the cement particles are too small, too large specific surface area of cement paste to demand the same flow too much, but the impact of the cement strength..Question: why is it necessary to make cement standard consistency before determining the setting time and soundness of cement?.The setting time stability of cement is related to the water cement ratio of cement paste. Although the water consumption is too large, the hydration speed of cement increases, but the distance between the cement particles increases and the setting time of the cement increases. When the cement stability betweenqualified and unqualified, and increase the water cement ratio, the soundness of cement performance is qualified. Therefore, the water content of cement standard consistency is determined first, and the setting time and soundness of cement are determined by the same conditions..Question: why concrete is not the amount of cement as much as possible?.When the amount of cement is too large, the shrinkage of concrete is greater and the hydration heat is larger, which leads to the cracking of concrete. At the same time waste cement, increase project costs..Question: why is it necessary to add a certain amount of cementitious material to cement mortar?.Because the cement is used for making mortar, the mark of the cement is much larger than the strength grade of the mortar, so a small amount of cement can meet the requirement of strength. However, when the amount of cement is less (such as less than 350 kg), the fluidity and water holding capacity of mortar are often poor, especially the water retention. Therefore, the construction quality of mortar is seriously affected, so it is necessary to add some other cheap cementing material to improve the fluidity of mortar, especially the water retention..Question: under the condition that the amount of cement slurry is certain, why is the rate of sand too small and too big tomake the fluidity of mixture become worse?.The dosage of cement slurry under certain conditions, when the void volume rate of sand is not enough to fill the number of hours of gravel or little surplus, in this case, the stone mortar at the contact point is too little, flowing mixture is very small. When the sand ratio is too large, set the total surface area and void material consumption rate increases, the fine aggregate used for wrapping the surface of cement mortar increased, cement sand at the point of contact is insufficient, even not enough to cover all the sand slurry, the dry mortar, liquidity mixture becomes worse..Question: what is the yield point of the material instead of its tensile strength as a basis for the design of the structure?.Yield strength and ultimate tensile strength are two important indexes to evaluate the strength of steel. Ultimate tensile strength is the maximum stress that a test piece can bear. In the structural design, the component is required to work within the elastic deformation range, even if a small amount of plastic deformation should be avoided, so the yield strength of the steel is taken as the basis for design stress. Tensile strength can not be fully utilized in structural design, but the ratio of yield strength to tensile strength (bending strength ratio) has some significance. The smaller the yield strength ratio is, the higher the structural safety is..Question: why is the elongation of steel an important technical performance index for construction steel?.Steel in use, in order to avoid the normal stress at the defect stress concentration due to brittle fracture, its plasticity is good, which has a certain elongation, the defect can be more than the yield point of the material, with the plastic deformation and the stress redistribution, and avoid the premature failure of steel. At the same time, under normal temperature, the steel is processed into a certain shape, and it also requires a certain plasticity. But the elongation can not be too large, otherwise it will allow the use of steel in excess of the allowable deformation value..Question: why does cold working hardening of steel have side effects of plasticity and brittleness?.Steel processing and plastic deformation, the plastic deformation of grains within the region have a relative slip, the slip surface of grain crushing, lattice deformation, a sliding surface is uneven, and the distortion to the difficult. Therefore, the plasticity decreases and the brittleness increases..Question: what are the similarities and differences between porous bricks and hollow bricks?.The two kinds of brick porosity requirements are equal to or greater than 15%; the brick hole size is small and the number of hollow brick the size of the hole and the number of small; the porous brick used in load-bearing hollow brick, often used for non load bearing parts..Question: in a water aerated concrete block masonry wall immediately after pouring mortar plastering mortar layer, prone to cracking and hollowing and why?.Aerated concrete block of the pores are mostly "ink bottle" structure, only a small part of the pores formed by evaporation of water, small belly, capillary action is poor, so water absorption heat conduction slow. Ordinary brick fired water easily absorb enough water, and aerated concrete surface watering a lot, but in fact, water absorption is not much. In general the mortar plastering of aerated concrete is easy to absorb moisture, and is easy to produce cracking and hollowing. Therefore, the water can be divided into several times, and the mortar with good water retention and high bond strength is adopted..Question: why should lightweight aggregate concrete small hollow block be used for expansion joint when wall is used?.This is because the temperature deformation and dry shrinkage deformation of lightweight aggregate concrete small hollow block are larger than that of sintered common brick. In order to prevent cracks, the expansion joint can be set according to specific conditions, and the structural reinforcement is added to the necessary parts..Question: are stone materials available for underground foundations?.Not always。
混凝土碳化研究与进展(2)--碳化速度的影响因素及碳化对混凝土品质的影响

Pore solution.Pore structure of mortar is a key factor which determines the progress of carbonation by affecting diffusivity of
permeability CCh and
of water.The reaction between cch and hydration products may not occur without the presence of water.
[收稿日期]2005—08—15
· 10 万· 方数据
带来一些变化。因此,分析混凝土的碳化规律,研究 碳化引起的混凝土结构和性能的变化对于混凝土结 构的耐久性研究具有重要的意义。
1 混凝土碳化速度的影响因素
一般来说混凝土的碳化速度可用碳化深度和碳 化时间之间的关系来表示。碳化深度与碳化时间的 平方根大致成正比C=A√t。这里,碳化速度系数A 是决定于许多外因和内因的复杂函数。 1.1外因 1.1.1环境温度混凝土构筑物所处的环境温度越 高,C02在混凝土中的扩散速度及C02与水化产物的 反应速度越快,碳化速度加快。 1.1.2湿度 日本学者对水中养护7d的混凝土在 不同湿度条件下养护16年后认为相对湿度50%~ 60%范围内碳化速度最快,如图1所示。湿度较小 时,混凝土处于较为干燥或含水率较低的状态,虽然
图2水泥含碱量与碳化深度的关系[71
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吕 ¥ 世 蠖 Z o
图3 NaCl掺量对孔溶液OH一浓度的影响‘7
NaCl掺量/(kg/m3)
图4 NaCl对碳化速度的影响[8】 1.2.5孔隙水迁移和浓缩 含碱量高的混凝土毛细
孔溶液有迁移和浓缩时,暴露于大气中的混凝土表面
混凝土强度尺寸效应综述

总752期第十八期2021年6月河南科技Journal of Henan Science and Technology混凝土强度尺寸效应综述鲁猛王昊刘泽鹏席君毅(华北水利水电大学土木与交通学院,河南郑州450045)摘要:混凝土强度尺寸效应是当前混凝土在大型结构应用时亟待解决的问题之一。
本文介绍混凝土抗压强度、劈裂抗拉强度、耐久性以及断裂性能随试样高度、直径、形状变化的规律,并对有关混凝土强度尺寸效应研究的进一步发展提出相关建议。
关键词:混凝土;尺寸效应;抗压强度;劈裂抗拉强度中图分类号:TU528文献标识码:A文章编号:1003-5168(2021)18-0095-03Review on Size Effect of Concrete StrengthLU Meng WANG Hao LIU Zepeng XI Junyi(School of Civil Engineering and Communications,North China University of Water Resources and Electric Power,ZhengzhouHenan450045)Abstract:The size effect of concrete strength is one of the urgent problems to be solved when concrete is applied in large-scale structures.This paper introduces the variation of compressive strength,splitting tensile strength,durabili⁃ty and fracture properties of concrete with the height,diameter and shape of samples.Finally,some suggestions are put forward for the further development of the review on the size effect of concrete strength.Keywords:concrete;size effect;compressive strength;splitting tensile strength混凝土尺寸效应是指混凝土性能随其几何尺寸的变化而变化。
贝塔粒子表面面积分析仪 TriStar II Plus 说明书

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The system includes a mobile platform which easily rolls from location to location.Additional accessories are available for special applications.To request a quote or additional product information, visitMicromeritics web site at , contact your local Micromeritics sales representative or our Customer Service Department at (770) 662-3636External Sample Preparation DevicesModel 021 LN2 Transfer SystemLN 2 Transfer SystemPharmaceuticals - Surface area and porosity play major roles in the purification, process-ing, blending, tableting, and packaging of pharmaceutical products as well as their useful shelf life, dissolution rate, and bioavailability.Ceramics - Surface area and porosity affect the curing and bonding of greenware and influence strength, texture, appearance, and density of finished goods. The surface area of glazes and glass frits affects shrinkage, crazing, and crawling.Adsorbents - Knowledge of surface area, total pore volume, and pore size distribution is important for quality control of industrial adsorbents and in the development of separation processes. Surface area and porosity characteristics affect the selectivity of an adsorbent. Activated Carbons - Surface area and porosity must be optimized within narrow ranges to accomplish gasoline vapor recovery in automobiles, solvent recovery in painting opera-tions, or pollution controls in wastewater management.Carbon Black - The wear lifetime, traction, and performance of tires are related to the surface area of carbon blacks used in their production.Catalyst -The active surface area and pore structure of catalysts influence production rates. Limiting the pore size allows only molecules of desired sizes to enter and exit, creating a selective catalyst that will produce primarily the desired product.Paints and Coatings - The surface area of a pigment or filler influences the gloss, texture, color, color saturation, brightness, solids content, and film adhesion properties. Theporosity of a print media coating is important in offset printing where it affects blistering, ink receptivity, and ink holdout.Projectile Propellant - The burn rate of propellants is a function of surface area. Too high a rate can be dangerous; too low a rate can cause malfunction and inaccuracy.Medical Implants - Controlling the porosity of artificial bone allows it to imitate real bone that the body will accept and allow tissue to be grown around it.Electronics - By selecting high surface area material with carefully designed porenetworks, manufacturers of super-capacitors can minimize the use of costly raw materials while providing more exposed surface area for storage of charge.Cosmetics - Surface area is often used by cosmetic manufacturers as a predictor of particle size when agglomeration tendencies of the fine powders make analysis with a particle-sizing instrument difficult.Aerospace - Surface area and porosity of heat shields and insulating materials affect weight and function.Geoscience - Porosity is important in groundwater hydrology and petroleum exploration because it relates to the quantity of fluid that a structure can contain as well as how much effort will be required to extract it.Nanotubes - Nanotube surface area and microporosity are used to predict the capacity of a material to store hydrogen.Fuel Cells - Fuel cell electrodes require high surface area with controlled porosity to produce optimum power density.ApplicationsTriStar II Plus。
microporous mesoporous mater影响因子 -回复

microporous mesoporous mater影响因子-回复Microporous and mesoporous materials are a class of materials that have unique porous structures. These structures play a crucial role in determining their properties and potential applications. In this article, we will explore the factors that influence the properties of microporous and mesoporous materials, with a focus on their impact on their corresponding impact factors.Impact Factor:Before we delve into the factors that influence the impact factor of microporous and mesoporous materials, let's first understand what impact factor means. Impact factor is a measure of the influence a scientific journal has in its field. It is calculated by the ratio of the number of citations an article receives in a particular year to the total number of articles published in the journal in the previous two years. The impact factor of a journal is often used as an indicator of the prestige and significance of the research published in that journal.Now that we have defined impact factor, let's explore the factors that influence it.1. Porosity and Pore Size:Microporous and mesoporous materials owe their unique properties to their porous structures. Porosity refers to the presence of void spaces within the material's structure, while pore size determines the size of these void spaces. Both porosity and pore size significantly influence the impact factor of these materials.A high porosity allows for a larger surface area, which in turn increases the likelihood of interactions with other molecules or particles. This increased surface area enhances the material's adsorption, catalytic, and separation capabilities, making it more valuable to the scientific community. Consequently, materials with higher porosity often have higher impact factors.Similarly, the size of the pores is crucial because different applications require different pore sizes. For instance, larger mesopores are typically more suitable for adsorption or separation processes, while smaller micropores are ideal for gas storage or molecular sieving. Materials with a well-defined pore size distribution that aligns with the desired application tend to havemore significant impacts and thus higher impact factors.2. Surface Chemistry and Functionality:The surface chemistry and functionality of microporous and mesoporous materials also play a vital role in their impact factor. The chemical composition and functional groups present on the material's surface influence its interaction with other substances.Functional groups can be tailored to enhance specific properties, such as selectivity or catalytic activity. For example, the introduction of specific functional groups can enhance a material's ability to specifically adsorb certain molecules or catalyze specific reactions. These tailored surface functionalities make the material highly desirable for researchers in various fields and contribute to a higher impact factor.3. Synthesis Techniques and Structure Control:The synthesis techniques employed to prepare microporous and mesoporous materials are critical in determining their structure and, consequently, their properties. Various methods, such as templating, sol-gel, and hydrothermal synthesis, can be used to control the size, shape, and distribution of pores in the material.Precise control of the material's pore structure allows for tailoring their properties to specific applications. Materials with well-defined structures and high uniformity tend to have higher impact factors as they demonstrate reproducibility and reliability, making them attractive to the scientific community.4. Characterization and Evaluation:Accurate characterization of microporous and mesoporous materials is essential for evaluating their properties and performance. Characterization techniques such as nitrogen adsorption, X-ray diffraction, and electron microscopy provide valuable information about a material's porosity, surface area, crystallinity, and morphology.Accurate and thorough characterization enhances the credibility and reliability of the research published on these materials. Consequently, articles reporting on microporous and mesoporous materials with comprehensive characterization studies tend to have higher impact factors.In conclusion, several factors influence the impact factor ofmicroporous and mesoporous materials. These include porosity and pore size, surface chemistry and functionality, synthesis techniques and structure control, as well as characterization and evaluation. Understanding these factors is vital for researchers working in this field to optimize their material's properties and maximize its impact on the scientific community.。
分等级大微孔、介孔大孔

ARTICLEOPENReceived11Dec2012|Accepted16May2013|Published14Jun2013A solid with a hierarchical tetramodalmicro-meso-macro pore size distributionYu Ren1,Zhen Ma2,3,Russell E.Morris1,Zheng Liu1,Feng Jiao4,Sheng Dai3&Peter G.Bruce1Porous solids have an important role in addressing some of the major energy-related pro-blems facing society.Here we describe a porous solid,a-MnO2,with a hierarchical tetramodalpore size distribution spanning the micro-,meso-and macro pore range,centred at0.48,4.0,18and70nm.The hierarchical tetramodal structure is generated by the presence ofpotassium ions in the precursor solution within the channels of the porous silica template;thesize of the potassium ion templates the microporosity of a-MnO2,whereas theirreactivity with silica leads to larger mesopores and macroporosity,without destroying themesostructure of the template.The hierarchical tetramodal pore size distribution influencesthe properties of a-MnO2as a cathode in lithium batteries and as a catalyst,changingthe behaviour,compared with its counterparts with only micropores or bimodalmicro/mesopores.The approach has been extended to the preparation of LiMn2O4with ahierarchical pore structure.1EaStCHEM,School of Chemistry,University of St Andrews,St Andrews KY169ST,UK.2Shanghai Key Laboratory of Atmospheric Particle Pollution and Prevention(LAP3),Department of Environmental Science and Engineering,Fudan University,Shanghai200433,China.3Chemical Sciences Division,Oak Ridge National Laboratory,Oak Ridge,T ennessee37831,USA.4Department of Chemical and Biomolecular Engineering,University of Delaware,Newark,Delaware19716,USA.Correspondence and requests for materials should be addressed to P.G.B.(email:p.g.bruce@).P orous solids have an important role in addressing some of the major problems facing society in the twenty-first century,such as energy storage,CO2sequestration,H2 storage,therapeutics(for example,drug delivery)and catalysis1–8. The size of the pores and their distribution directly affect their ability to function in a particular application2.For example, zeolites are used as acid catalysts in industry,but their micropores impose severe diffusion limitations on the ingress and egress of the reactants and the catalysed products9.To address such issues, great effort is being expended in preparing porous materials with a bimodal(micro and meso)pore structure by synthesizing zeolites or silicas containing micropores and mesopores10–17,or microporous metal–organic frameworks with ordered mesopores18.Among porous solids,porous transition metal oxides are particularly important,because they exhibit many unique properties due to their d-electrons and the variable redox state of their internal surfaces8,19–22.Here we describe thefirst solid(a-MnO2)possessing hierarchical pores spanning the micro,meso and macro range, centred at0.48,4.0,18and70nm.The synthesis method uses mesoporous silica as a hard template.Normally such a template generates a mesoporous solid with a unimodal23–31or,at most,a bimodal pore size distribution32–38.By incorporating Kþions in the precursor solution,within the silica template,the Kþions act bifunctionally:their size templates the formation of the micropores in a-MnO2,whereas their reactivity with silica destroys the microporous channels in KIT-6comprehensively, leading to the formation of a-MnO2containing large mesopores and,importantly,macropores,something that has not been possible by other methods.Significantly,this is achieved without destroying the silica template by alkaline ions.The effect of the tetramodal pore structure on the properties of the material is exemplified by considering their use as electrodes for lithium-ion batteries and as a catalyst for CO oxidation and N2O decomposition.The novel material offers new possibilities for combining the selectivity of small pores with the transport advantages of the large pores across a wide range of sizes.We also present results demonstrating the extension of the method to the synthesis of LiMn2O4with a hierarchical pore structure.ResultsComposition of tetramodal a-MnO2.The composition of the synthesized material was determined by atomic absorption ana-lysis and redox titration to be K0.08MnO2(the K/Mn ratio of the precursor solution was1/3).The material is commonly referred to as a-MnO2,because of the small content of Kþ19.N2sorption analysis of tetramodal a-MnO2.The tetramodal a-MnO2shows a type IV isotherm(Fig.1a).The pore size dis-tribution(Fig.1b)in the range of0.3–200nm was analysed using the density functional theory(DFT)method applied to the adsorption branch of the isotherm39–42,as this is more reliable than analysing the desorption branch43;note that this is not the DFT method used in ab initio electronic structure calculations. Plots were constructed with vertical axes representing ‘incremental pore volume’and‘incremental surface area’.Large (macro)pores can account for a significant pore volume while representing a relatively smaller surface area and vice versa for small(micro)pores.Therefore,when investigating a porous material with a wide range of pore sizes,for example,micropore and macropore,the combination of surface area and pore volume is essential to determine the pore size distribution satisfactorily (Fig.1b).Considering both pore volume and surface area, significant proportions of micro-,meso-and macropores are evident,with distinct maxima centred at0.70,4.0,18and70nm.To probe the size of the micropores more precisely than is possible with DFT,the Horvath–Kawazoe pore size distribution analysis was employed44.A single peak was obtained at0.48nm(Fig.1c),in good accord with the0.46-nm size of the2Â2channels of a-MnO2 (refs.19,21).The relatively small Brunauer–Emmett–Teller(BET) surface area of tetramodal a-MnO2(79–105m2gÀ1; Supplementary Table S1)compared with typical surface areas of mesoporous metal oxides(90–150m2gÀ1)45is due to the significant proportion of macropores(which have small surface areas)and relatively large(18nm)mesopores—a typical mesoporous metal oxide has only3–4nm pores.TEM analysis of tetramodal a-MnO2.Transmission electron microscopic(TEM)data for tetramodal a-MnO2,Fig.2, demonstrates a three-dimensional pore structure with a sym-metry consistent with space group Ia3d.From the TEM data,an a0lattice parameter of23.0nm for the mesostructure could be extracted,which is in good agreement with the value obtained from the low-angle powder X-ray diffraction(PXRD)data, a0¼23.4nm(Supplementary Fig.S1a).High-resolution TEM images in Fig.2c–e demonstrate that the walls are crystalline with a typical wall thickness of10nm.The lattice spacings of0.69,0.31 and0.35nm agree well with the values of6.92,3.09and3.46Åfor the[110],[310]and[220]planes of a-MnO2(International Centre for Diffraction Data(ICDD)number00-044-0141), respectively.The wide-angle PXRD data matches well with the PXRD data of bulk cryptomelane a-MnO2(Supplementary Fig. S1b),confirming the crystalline walls.The various pores in tetramodal a-MnO2can be observed by TEM directly:the0.48-nm micropores are seen in Fig.2e(2Â2 tunnels with dimensions of0.48Â0.48nm in the white box);the 4.0-nm pores are shown in Fig.2b–d;the18-nm pores are shown in Fig.2a;the70-nm pores are evident in Fig.2b(highlighted with white circles).Li intercalation.Li can be intercalated into bulk a-MnO2 (ref.46).Therefore,it is interesting to compare Li intercalation into bulk a-MnO2(micropores only)and bimodal a-MnO2 (micropores along with a single mesopore of diameter3.6nm,see Methods)with tetramodal a-MnO2(micro-,meso-and macropores).Each of the three a-MnO2materials was subjected to Li intercalation by incorporation as the positive electrode in a lithium battery,along with a lithium anode and a non-aqueous electrolyte(see Methods).The results of cycling(repeated intercalation/deintercalation of Li)the cells are shown in Fig.3. Although all exhibit good capacity to cycle Li at low rates of charge/discharge(30mA gÀ1),tetramodal a-MnO2shows sig-nificantly higher capacity(Li storage)at a high rate of 6,000mA gÀ1(corresponding to charge and discharge in3min). The tetramodal a-MnO2can store three times the capacity(Li) compared with bimodal a-MnO2,and18times that of a-MnO2 with only micropores,at the high rate of intercalation/deinter-calation(Fig.3).The superior rate capability of tetramodal a-MnO2over microporous and bimodal forms may be assigned to better Liþtransport in the electrolyte within the hierarchical pore structure of tetramodal a-MnO2.The importance of elec-trolyte transport in porous electrodes has been discussed recently35,47,48and the results presented here reinforce the beneficial effect of a hierarchical pore structure.Catalytic studies.CO oxidation and N2O decomposition were used as reactions to probe the three different forms of a-MnO2as catalysts(Supplementary Fig.S2).As shown in Supplementary Fig.S2a,tetramodal a-MnO2demonstrates better catalytic activity compared with only micropores or bimodal a-MnO2;thetemperature of half CO conversion (T 50)was 124°C for tetra-modal a -MnO 2,whereas microporous and bimodal a -MnO 2exhibited a T 50value of 275°C and 209°C,respectively.In the case of N 2O decomposition,a -MnO 2with only micropores demonstrated no catalytic activity in the range of 200–400°C,in accord with a previous report 49.Tetramodal and bimodal a -MnO 2showed catalytic activity and reached 32%and 20%of N 2O conversion,respectively,at a reaction temperature of 400°C.The differences in catalytic activity are related to the differences in the material.A detailed study focusing on the catalytic activity alonewould be necessary to demonstrate which specific features of the textural differences (pore size distribution,average manganese oxidation state,K þand so on)between the different MnO 2materials are responsible for the differences in behaviour.However,the preliminary results shown here do illustrate that such differences exist.Porous LiMn 2O 4.To demonstrate the wider applicability of the synthesis method,LiMn 2O 4with a hierarchical pore structurewas1801601401201008060402000.00.20.40.60.81.0V (c m 3 g –1)Pore diameter (nm)0.0120.0100.0080.0060.0040.0020.000I n c r e m e n t a l p o r e v o l u m e (c m 3 g –1)Pore width (nm)I n c r e m e n t a l s u r f a c e a r e a (m 2 g –1)I n c r e m e n t a l s u r f a c e a r e a (m 2 g –1)P /P 0Figure 1|N 2sorption analysis of tetramodal a -MnO 2.(a )N 2adsorption–desorption isotherms,(b )DFT pore size distribution and (c )Horvath–Kawazoe pore size distribution from N 2adsorption isotherm for tetramodal a -MnO 2.Figure 2|TEM images of tetramodal a -MnO 2.TEM images along (a )[100]direction,showing 18nm mesopores (scale bar,50nm);(b )4.0and 70nm pores (70nm pores are highlighted by white circles;scale bar,100nm);(c –e )high-resolution (HRTEM)images of tetramodal a -MnO 2showing 4.0and 0.48nm pores (scale bar,10nm).Inset is representation of a -MnO 2structure along the c axis,demonstrating the 2Â2micropores as shown in the HRTEM (white box)in e .Purple,octahedral MnO 6;red,oxygen;violet,potassium.synthesized in a way similar to that of tetramodal a -MnO 2.The main difference is the use of LiNO 3instead of KNO 3(see Methods).In this case,Li þreacts with the silica template col-lapsing/blocking the microporous channels in the KIT-6and resulting in the large mesopores and macropores (17and 50nm)in the LiMn 2O 4obtained.The use of Li þinstead of the larger K þdeters the formation of micropores because Li þis too small.TEM analysis illustrates the hierarchical pore structure of LiMn 2O 4(Supplementary Fig.S3):4.0nm pores are evident in Supplementary Fig.S3b;17nm pores in Supplementary Fig.S3a;and 50nm pores in Supplementary Fig.S3b (highlighted with white circles).The d-spacing of 0.47nm in the high-resolution TEM image (Supplementary Fig.S3c)is in good accordance with the values of 0.4655nm for the [111]planes of LiMn 2O 4(ICDD number 00-038-0789)and with the wide-angle PXRD data (Supplementary Fig.S4).The original DFT pore size distribution analysis from N 2sorption (adsorption branch)gives three pore sizes in the range of 1–100nm centred at 4.0,17and 50nm (Supplementary Fig.S5).A more in-depth presentation of the results for LiMn 2O 4will be given in a future paper;preliminary results presented here illustrate that the basic method can be applied beyond a -MnO 2.DiscussionTurning to the synthesis of the tetramodal a -MnO 2,the details are given in the Methods section.Hard templating using silica templates,such as KIT-6,normally gives rise to materials with unimodal or,at most,bimodal mesopore structures,and in the latter case the smaller mesopores dominate over the larger mesopores 8,32,35.Alkali ions are excellent templates for micropores in transition metal oxides 19,21,but they have been avoided in nanocasting from silica templates because of concerns that they would react with and,hence,destroy thesilica20018016014012010080604020D i s c h a r g e c a p a c i t y (m A h g –1)0Cycle numberx in Li x MnO 2Figure 3|Electrochemical behaviour of different a -MnO 2.Capacity retention for tetramodal a -MnO 2cycled at 30(empty blue circles)and 6,000mA g À1(filled blue circles);bulk a -MnO 2cycled at 30(empty red squares)and 6,000mA g À1(filled red squares);bimodal a -MnO 2cycled at 30(empty black triangle)and 6,000mA g À1(filled blacktriangles).18 nm pores70 nm poresTwo sets of mesoporeschannels connecting both sets of mesoporesEtching of silica Etching of silica Etching of silica template2discontinuously within one set of the KIT-6mesoporesFigure 4|Formation mechanism of meso and macropores in tetramodal a -MnO 2.When both KIT-6mesochannels are occupied by a -MnO 2and then the silica between them etched away,the remaining pore is 4nm (centre portion of figure).When a -MnO 2grows in only one set of mesochannels and then the KIT-6is dissolved away,the remaining metal oxide has 18nm pores (upper portion of figure).The comprehensive destruction of the microchannels in KIT-6by K þleads to a -MnO 2growing in only a proportion of one set of the KIT-6mesochannels,resulting in the formation of B 70nm pores (lower portion of figure).template50.Here,not only have alkali ions been used successfully in precursor solutions without destroying the template mesostructure but they give rise to macropores in the a-MnO2, thus permitting the synthesis of a tetramodal,micro-small,meso-large,meso-macro pore structure.Synthesis begins by impregnating the KIT-6silica template with a precursor solution containing Mn2þand Kþions.On heating,the Kþions template the formation of the micropores in a-MnO2,as the latter forms within the KIT-6template.KIT-6 consists of two interpenetrating mesoporous channels linked by microporous channels51–53.The branches of the two different sets of mesoporous channels in KIT-6are nearest neighbours separated by a silica wall of B4nm53;therefore,when both KIT-6mesochannels are occupied by a-MnO2and the silica between them etched away,the remaining pore is4nm(see centre portion of Fig.4).It has been shown previously,by a number of authors,that by varying the hydrothermal conditions used to prepare the KIT-6,the proportion of the microchannels can be decreased to some extent,thus making it difficult to simultaneouslyfill the neighbouring KIT-6mesoporous channels by the precursor solution of the target mesoporous metal oxide33–35.As a result,the target metal oxide grows in only one set of mesochannels of the KIT-6host but not both.When the KIT-6is dissolved away,the remaining metal oxide has B18nm pores,because the distance between adjacent branches of the same KIT-6mesochannels is greater than between the two different mesochannels in KIT-6.Here we propose that the Kþions have a similar effect on the KIT-6to that of the hydrothermal synthesis,but by a completely different mechanism.Reaction between the Kþions in the precursor solution with the silica during calcination results in the formation of Kþ-silicates,which cause collapse or blocking of the microporous channels in KIT-6,such that the a-MnO2grows in one set of the KIT-6mesochannels,giving rise to18nm pores in a-MnO2when the silica is etched away,see top portion of Fig.4. However,the reaction between Kþand the silica is more severe than the effect of varying the hydrothermal treatment.In the former case,the KIT-6microchannels are so comprehensively destroyed that the proportion of the large(18nm)to smaller (4nm)mesopores is greater than can be achieved by varying hydrothermal conditions.The comprehensive destruction of the microchannels in KIT-6by Kþ,perhaps augmented by some minor degradation of parts of the mesochannels,leads to a-MnO2 growing in only a proportion of one set of the KIT-6 mesochannels,resulting in the formation of B70nm pores in a-MnO2,see lower portion of Fig.4.In summary,the Kþreactivity with the silica goes beyond what can be achieved by varying the conditions of hydrothermal synthesis and is responsible for generating the tetramodal pore size distribution reported here. The mechanism of pore formation in a-MnO2by reaction between Kþand the silica template is supported by several findings.First,by the lower K/Mn molar ratio of thefinal tetramodal a-MnO2product(0.08)compared with the starting materials(0.33)implies that some of the Kþions in the impregnating solution have reacted with the silica.Second, support for collapse/blocking of the microporous channels in KIT-6due to reaction with Kþwas obtained by comparing the texture of KIT-6impregnated with an aqueous solution contain-ing only KNO3and calcined at300and500°C.The micropore volume in KIT-6is the greatest,with no KNO3in the solution;it then decreases continuously as the calcination temperature and calcination time is increased,such that after2and5h at500°C the micropore volume has decreased to zero(Supplementary Fig. S6).Third,we prepared tetramodal a-MnO2using a similar synthetic procedure to that described in the Methods section, except that this time we used a covered tall crucible for the calcination step.Sun et al.54have shown that using a covered,tall crucible when calcining results in porous metal oxides with much larger particle sizes.If the70-nm pores had arisen simply from the gaps between the particles,then the pore size would have changed;in contrast,it remained centred at70nm, Supplementary Fig.S7,consistent with the70-nm pores being intrinsic to the materials and arising from reaction with the Kþas described above.Fourth,if the synthesis of MnO2is carried out using the KIT-6template but in the absence Kþions,then the DFT pore size distribution shown in Supplementary Fig.S8is obtained.The0.48-and70-nm pores are now absent,but the4-and18-nm pores remain.This demonstrates the key role of Kþin the formation of the smallest and largest pores and,hence,in generating the tetramodal pore size distribution.The absence of Kþmeans that there is nothing to template the0.48nm pores and so a-MnO2is not formed;the b-polymorph is obtained instead.The absence of Kþalso means that the microchannels in the KIT-6template remain intact,resulting in no70nm pores and the dominance of the4-nm pores compared with the 18-nm pores.The hierarchical pore structure can be varied systematically by controlling the synthesis conditions,in particular the Kþ/Mn ratio of the precursor solution.A range of Kþ/Mn ratios,1/5,1/3and1/2,gave rise to a series of pore size distributions,in which the pore sizes remained the same but the relative proportions of the different pores varied (Supplementary Table S1).The higher the Kþ/Mn ratio,the greater the proportion of macropores and large mesopores.This is in accord with expectations,as the higher the Kþconcentra-tion in the precursor solution the greater the collapse/blocking of the microporous channels in the KIT-6(as noted above),and hence the greater the proportion of macropores and large mesopores.Indeed,these results offer further support for the mechanism of pore size distribution arising from reaction between Kþand the silica template.In conclusion,tetramodal a-MnO2,thefirst porous solid with a tetramodal pore size distribution,has been synthesized.Its hierarchical pore structure spans the micro,meso and macropore range between0.3and200nm,with pore dimensions centred at 0.48,4.0,18and70nm.Key to the synthesis is the use of Kþions that not only template the formation of micropores but also react with the silica template,therefore,breaking/blocking the micro-porous channels in the silica template far more comprehensively than is possible by varying the hydrothermal synthesis conditions, to the extent that macropores are formed,and without destroying the silica mesostructure by alkali ions,as might have been expected.The resulting hierarchical tetramodal structure demon-strates different behaviours compared with microporous and bimodal a-MnO2as a cathode material for Li-ion batteries,and when used as a catalyst for CO oxidation and N2O decomposi-tion.The method has been extended successfully to the preparation of hierarchical LiMn2O4.MethodsSynthesis.Tetramodal a-MnO2(surface area96m2gÀ1,K0.08MnO2)was pre-pared by two-solvent impregnation55using Kþand mesoporous silica KIT-6as the hard template.KIT-6was prepared according to a previous report (hydrothermal treatment at100°C)51.In a typical synthesis of tetramodal a-MnO2, 7.53g of Mn(NO3)2Á4H2O(98%,Aldrich)and1.01g of KNO3(99%,Aldrich)were dissolved in B10ml of water to form a solution with a molar ratio of Mn/K¼3.0. Next,5g of KIT-6was dispersed in200ml of n-hexane.After stirring at room temperature for3h,5ml of the Mn/K solution was added slowly with stirring.The mixture was stirred overnight,filtered and dried at room temperature until a completely dried powder was obtained.The sample was heated slowly to500°C (1°C minÀ1),calcined at that temperature for5h with a cover in a normal crucible unless is specified54and the resulting material treated three times with a hot aqueous KOH solution(2.0M),to remove the silica template,followed by washing with water and ethanol several times,and then drying at60°C.Bimodal a-MnO2(surface area58m2gÀ1,K0.06MnO2)with micropore and a single mesopore size of3.6nm was prepared by using mesoporous silica SBA-15as a hard template.The SBA-15was prepared according to a previous report56.Bulk a-MnO2(surface area8m2gÀ1,K0MnO2)was prepared by the reaction between325mesh Mn2O3(99.0%,Aldrich)and6.0M H2SO4solution at80°C for 24h,resulting in the disproportionation of Mn2O3into a soluble Mn2þspecies and the desired a-MnO2product46.Treatment of KIT-6with KNO3was carried out as follows:1.01g of KNO3was dissolved in B15ml of water to form a KNO3solution.Five grams of mesoporous KIT-6was dispersed in200ml of n-hexane.After stirring at room temperature for 3h,5ml of KNO3solution was added slowly with stirring.The mixture was stirred overnight,filtered and dried at room temperature until a completely dried powder was obtained.The sample was heated slowly to300or500°C(1°C minÀ1), calcined at that temperature for5h and the resulting material was washed with water and ethanol several times,and then dried at60°C overnight.The synthesis method for hierarchical porous LiMn2O4was similar to that of tetramodal a-MnO2.The main difference was to use1.01g of LiNO3instead of KNO3.After impregnation into KIT-6,calcination and silica etching,porous LiMn2O4was obtained.Characterization.TEM studies were carried out using a JEOL JEM-2011, employing a LaB6filament as the electron source,and an accelerating voltage of 200keV.TEM images were recorded by a Gatan charge-coupled device camera in a digital format.Wide-angle PXRD data were collected on a Stoe STADI/P powder diffractometer operating in transmission mode with Fe K a1source radiation(l¼1.936Å).Low-angle PXRD data were collected using a Rigaku/MSC,D/max-rB with Cu K a1radiation(l¼1.541Å)operating in reflection mode with a scintillation detector.N2adsorption–desorption analysis was carried out using a Micromeritics ASAP2020.The typical sample weight used was100–200mg. The outgas condition was set to300°C under vacuum for2h,and all adsorption–desorption measurements were carried out at liquid nitrogen tem-perature(À196°C).The original DFT method for the slit pore geometry was used to extract the pore size distribution from the adsorption branch usingthe Micromeritics software39–42.A Horvath–Kawazoe method was used to extract the microporosity44.Mn and K contents were determined by chemical analysis using a Philips PU9400X atomic adsorption spectrometer.The average oxidation state of framework manganese in a-MnO2samples was determined by a redoxtitration method57.Electrochemistry.First,the cathode was constructed by mixing the active material (a-MnO2),Kynar2801(a copolymer based on polyvinylidenefluoride),and Super S carbon(MMM)in the weight ratio80:10:10.The mixture was cast onto Al foil (99.5%,thickness0.050mm,Advent Research Materials,Ltd)from acetone using a Doctor-Blade technique.After solvent evaporation at room temperature and heating at80°C under vacuum for8h,the cathode was assembled into cells along with a Li metal anode and electrolyte(Merck LP30,1M LiPF6in1:1v/v ethylene carbonate/dimethyl carbonate).The cells were constructed and handled in anAr-filled MBraun glovebox(O2o0.1p.p.m.,H2O o0.1p.p.m.).Electrochemical measurements were carried out at30°C using a MACCOR Series4200cycler.Catalysis.Catalytic CO oxidation was tested in a plug-flow microreactor(Alta-mira AMI200).Fifty milligrams of catalyst was loaded into a U-shaped quartz tube (4mm i.d.).After the catalyst was pretreated inflowing8%O2(balanced with He) at400°C for1h,the catalyst was then cooled down,the gas stream switched to1% CO(balanced with air)and the reaction temperature ramped using a furnace(at a rate of1°C minÀ1above ambient temperature)to record the light-off curve.The flow rate of the reactant stream was37cm3minÀ1.A portion of the product stream was extracted periodically with an automatic sampling valve and was analysed using a dual column gas 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陶土-粉煤灰基吸附性陶瓷基体的制备及其吸附性能
陶土-粉煤灰基吸附性陶瓷基体的制备及其吸附性能徐姗姗;魏刚;张晓丰;魏云鹏;张小冬;乔宁【摘要】Clay and modified fly ash have been used as raw materials to prepare a ceramic support with adsorption functionality by a half-dry pressing molding process. The influence of the raw material pretreatment, ratio of raw materials and sintering temperature on the adsorption properties, porosity, and strength of the ceramic support has been studied. The optimum preparation conditions were found to be; a mass ratio of clay and modified fly ash of 8:2, a heating rate of 1℃/min, and a sintering temperature of 900℃. Under these conditions, the porosity of the ceramic support was 36. 75% , the pore size distribution was in the range of 5 - 27 nm, the pure water flux was 52. 89 L/( m2 ·h), and the compressive strength was 17. 923 MPa. The results of treating solutions of rhodamine B, methylene blue, and Congo red, as well as analogue printing and dyeing wastewater and solutions containing PO43-and Fe2+ showed that the ceramic support had good adsorption and retention properties.%以陶土和改性粉煤灰为原料,采用半干压成型工艺制备了吸附性陶瓷基体.研究了原料预处理、配比、烧成温度等对陶瓷基体性能的影响,确定了最佳制备条件:陶土和改性粉煤灰质量比8∶2,升温速率1℃/min,烧成温度900℃.在此条件下制得的陶瓷基体的孔隙率为36.75%,孔径分布区间在5~ 27 nm,纯水通量52.89L/(m2·h),压缩强度17.923 MPa.对罗丹明B、亚甲蓝、刚果红模拟印染废水、含PO43-废水和含Fe2+废水的处理结果表明,所制备的陶瓷基体具有良好的吸附和截留性能.【期刊名称】《北京化工大学学报(自然科学版)》【年(卷),期】2012(039)004【总页数】5页(P42-46)【关键词】陶土;粉煤灰;多孔陶瓷基体;吸附性【作者】徐姗姗;魏刚;张晓丰;魏云鹏;张小冬;乔宁【作者单位】北京化工大学材料科学与工程学院化工资源有效利用国家重点实验室,北京100029;北京化工大学材料科学与工程学院化工资源有效利用国家重点实验室,北京100029;北京化工大学材料科学与工程学院化工资源有效利用国家重点实验室,北京100029;北京化工大学材料科学与工程学院化工资源有效利用国家重点实验室,北京100029;北京化工大学材料科学与工程学院化工资源有效利用国家重点实验室,北京100029;北京化工大学材料科学与工程学院化工资源有效利用国家重点实验室,北京100029【正文语种】中文【中图分类】TQ174.7陶瓷基体因具有抗高温高压、耐酸碱、机械强度大、能够长期稳定进行分离操作等优点在膜分离技术领域得到了广泛的应用[1]。
金属有机骨架材料对印染废水中染料和Cr(Ⅵ)的去除
在为国内印染废水治理研究提供一些参考和借鉴。
MOFs 复合材料的可见光吸收范围,复合材料的异质结特征
1 MOFs 材料对染料的光催化降解
室温搅拌法制备了一种新的可见光驱动型 g-C3N4/MIL-53
1.1 单一 MOFs 对染料的降解
MOFs 材料的合成方法十分简便,其由金属离子(金属
簇)与含羧基/氮原子等的芳香族有机配体通过形成牢固的
化 性 ,可 以 将 H2O2 分 子 氧 化 为 羟 基 自 由 基(·OH),而 在
的固态多孔材料。其孤立且均匀有序分布的半导体量子点
自由基(O2·-)。两种高氧化性的自由基物种可以将与 MOFs
MOFs)是由金属节点与多齿有机配体通过配位键组装形成
(金属节点)或光吸收天线(芳香性有机配体)在光激发下可
金属有机骨架材料对印染废水中染料和 Cr(VI)的去除
印 染(20水中染料和 Cr(VI)的去除
陈灵辉 1,李 庆 1,管斌斌 1,朱 炜 1,徐宇婷 1,樊增禄 2
æ1.西安工程大学 西安市纺织化工助剂重点实验室,环境与化学工程学院,陕西 西安 710048;
还原水体污染物,因经济性高、处理彻底、操作简便、环境友
好及利用太阳能备受瞩目。金属氧化物光催化剂 TiO2、ZnO
等可用于光催化降解染料,但其纳米级粉体使用时易流失、
67
印 染(2021 No.2)
难回收,且能带间隙宽、可见光利用率低。金属硫化物如
CdS、In2S3 等虽然可见光利用率较高,但易被光腐蚀引发重
略。而绝大多数的单一 MOFs 被证实在可见光驱动下的光
催化效能有待大幅提升。通过向 MOFs 空腔内引入高光敏
活性物种对其简单后修饰,以实现在可见光激发下对染料
土孔隙的分形几何研究_王清
土孔隙的分形几何研究*A Study on fractal of porosity in the soils王 清 王剑平(长春科技大学环境与建设工程学院,长春,130026) (南京水利科学研究院土工所,南京,210024)中图法分类号 P 642.1 文献标识码 A 文章编号 1000-4548(2000)04-0496-03作者简介 王 清,女,1959年生,教授,从事红土、黄土及软土等土体的工程地质及岩土工程研究工作。
1 前 言土中孔隙是土的重要性质之一[1],无论土体变形、土坡稳定性,还是地基承载力等都将直接或间接由土的孔隙来表示。
由于土体的多相性和不均匀性等,使测定各级孔隙及划分各级孔隙的研究极其复杂[2],为了更有效地研究土孔隙特征,本文采用了压汞测试法进行孔隙测定,并应用非线性理论之一———分形几何的观点来完成资料处理。
图1 黄土和黄土状土的孔隙分布特征图Fig .1 Pore size distribution of loess and loessial soil2 试验方法压汞试验是将已制好的土样通过不同压力将水银压入土体孔隙中,根据不同压力及所对应的进汞量(以汞饱和度计)绘制关系曲线(图1),了解不同孔隙大小(喉道半径)以及所占总孔隙体积的比例关系(表1)。
根据压汞曲线的特点,总结前人的研究经验[2~5],按照在一定范围内的孔隙具有相似的特性,通常将孔隙划分为大孔隙(d >4μm )、中孔隙(0.4μm <d ≤4μm )、小孔隙(0.04μm <d ≤0.4μm )和微孔隙(d ≤0.04μm )共4级,在此基础上对土体中孔隙的特性进行分析研究[3~5],压汞法解决了对集粒内孔隙测定存在着的难题,它是测定孔隙大小,尤其是定量测定微小孔隙的一种行之有效的方法。
它解决了许多理论和生产实际问题,也是一种较好的定量研究孔隙的方法之一。
3 分形理论的应用土体实际上是具有统计意义上的自相似的分形结构特征[6],采用统计自相似的方法来定量地描述复杂土体孔隙分布特征,从本质上揭示土体的变形性质及力学行为,为此,我们对压汞试验所测得的不同孔径数值采用双对数直角坐标来表示,其中X 轴表示孔径的大小,Y 轴表示大于某一孔径的累积百分含量,这样我们得到了一些所求的曲线(图2)。
水泥化学Cement Chemistry
Cement ChemistryCements:- used since historical times (Pyramids ≈3000 BC; Colosseum). Ancient cements of varying types. Two main classes of constructional cements are defined: non-hydraulic cements - do not set under water (see box), and hydraulic cement.Non-hydraulic cements were amongst the Array most common of the ancient cements.The relatively high solubilities ofportlandite (Ca(OH)2) and gypsum meansthat they deteriorate rapidly in moist orwet environments. The early Romansmade good use of lime based cements and mortars (cement + sand) by ramming the wetpastes to form a high density surface layer which carbonates in contact with air to producea low permeability surface skin of calcite. This protected the underlying Ca(OH)2andexamples of Roman lime mortars can still be seen in Hadrians Wall. Lime mortars were still used in domestic construction until relatively recently. Raw (natural) materials required temperature treatment. Partial dehydration of natural gypsum (≈200o C), and calcination of calcite (≈850o C). Hydraulic cements - more durable. Hydration products are very insoluble - cements set under water. Earliest systematic development of these, probably Roman - use of limestones containing silica and alumina and also use of volcanic earths as an additive to limestone prior to calcination. Forerunner of modern Portland cements.Portland cement - patented by Joseph Aspdin in mid-1800’s. Made from finely groundlimestone and finely divided clay to give a burned product containing 65-70% CaO, 18-24% SiO2, 3-8% Fe2O3, 3-8% Al2O3 plus smaller proportions of minor oxides (e.g. Na2O,K2O, MgO, etc.). Modern plants permit much more efficient processing and in addition,proportion raw mix compositions to produce a cement from which a range of strengthdevelopment and durability properties can be expected.Efficient grinding and blending of rawmaterials is essential. Firing of blends (raw meal ) takes place in a rotary kiln following drying and dehydration in cyclone preheaters and pre-calciners . Materials undergo solid state reaction and partial melting (clinkering) at temperatures of up to 1500C (in the hot zone of the kiln). Cement clinker is recovered on the cooling grate and sent for grinding and blending with gypsum. Cement clinker composition : - main clinker minerals are alite, belite, aluminate andferrite. Proportions vary depending on raw meal composition and firing and contribute to defining the hydration and strength development properties of the cement product. Alite - C 3S, 3CaO.SiO 2 (idealised): Minor - Al 2O 3, MgO, P 2O 5, Fe 2O 3, Na 2O, K 2O Belite - C 2S, 2CaO.SiO 2 (idealised): Minor - Al 2O 3, MgO, P 2O 5, Fe 2O 3, Na 2O, K 2O Aluminate - C 3A, 3CaO.Al 2O 3 (idealised): Minor - Fe 2O 3, SiO 2, MgO, Na 2O, K 2O Ferrite - C 4AF, 4CaO.Al 2O 3.Fe 2O 3 (idealised): Minor - SiO 2, MgO, TiO 2, Mn 2O 3.Chemistry of clinker formation: - information on raw meal composition and required kiln conditions may be obtained from equilibrium phase diagrams . Minor components have a small influence on equilibria but approximations can be made using the CaO-Al 2O 3-SiO 2-Fe 2O 3 diagram although it is perhaps preferable to restrict initial considerations to phase relations in the CaO-SiO 2 and the CaO-Al 2O 3-SiO 2 systems.The CaO-SiO 2 and CaO-Al 2O 3-SiO 2 systems are binary and ternary systems respectively. The ternary system shows the temperature and compositional information of the binary system (CaO-SiO 2) but with the third component (Al 2O 3) also, viewed from above. The curved lines represent temperature ‘valleys’ as on a map. Compositional information at a fixed temperature can be derived from an isothermal section . The 1500o C section of the CaO-Al 2O 3-SiO 2 system allows some consideration of phase equilibria in cement making.Approximate bulk composition of raw meal is represented by C which means that C 2S and C3S will be in equilibrium with a liquid phase of composition L c (which contains CaO, Al 2O 3 and SiO 2). It would expected from this diagram that the liquid would cool to crystallise C 3A. In practice, the final phase assemblage includes C 12A 7, a phase relevant to a lower temperature diagram. This arisesdue to the non-equilibrium effect of fractionation; as cooling occurs, slow reactions can cause high temperature assemblages to be frozen in). The final properties of the cement strongly depend on its mineral composition so that raw meal composition and firing conditions are adjusted depending on the type of cement to be produced (see later notes on Cement Type). The cement manufacturer expresses the product composition both as an oxide analyses (chemical) or mineral composition. The latter is calculated using the Bogue calculation .HYDRATION - the term used to describe a range of reactions between cement and water to produce a hardened product. A cement clinker particle is a multiphase solid havingmassive calcium silicate grains (50 - 100 μm) in a matrix of interstitial aluminate and(see box) to produce a range ofhydration products which intermeshand interleave to produce a dense andstrength developing solid. The ratesof reaction are important. The C3Areaction is fastest and also generatesmost heat (cement hydration isexothermic) but little contribution toultimate strength is derived from thisphase alone although it contributessignificantly to early strength. Theprincipal contributers to longer term strength are the calcium silicates. C3S is most reactive, giving early strength but C2S has a better longer term contribution. The C-S-H produced is the principal binding phase in Portland cements and is quantitatively the most significant hydration product. The ferrite reactions are intermediate in rate between the C3S and C2S reactions but have an important long term contribution to strength and durability.Properties of Cement Hydration ProductsCa(OH)2- crystalline, isostructural with thenatural mineral Portlandite. Solubility at 25o Cof around 1g.l-1.C-S-H - poorly crystalline product of variable composition. Considered to be based on a crumpled layer structure (analogous to a distorted clay sequence) which traps regions of porosity - pore size distribution from nm to μm. Simplified composition given by: Ca x H6-2x Si2O7.zCa(OH)2.nH2O where CaO/SiO2 = (x+z)/2 (Glasser et al, J.Am. Ceram. Soc., 70, 481-5, (1987)). Variable CaO/SiO2ratio (approx. 0.8 to 1.8) and variable H2O:SiO2 ratio (see CaO-SiO2-H2O phase diagram below). Variable composition means variable solubility properties. Solution compositions above C-S-H and the presence of other phases defines the C-S-H composition (see lectures) so that cements containing siliceous blending agents will have compositionally quite different C-S-H to that found in OPC pastes.Distribution of hydration products in Portlandcement pastes Rates of hydration of individual clinker phasesAF t - or ettringite, or aluminoferrite trisulphate (C 6AS 3H 32). Crystalline - trigonal. Forms columnar type structure consisting of (Al,Fe)(OH)6 octahedra alternating with triangular groups of edge sharing CaO 8 polyhedra with which they share OH - ions. Inter-column regions contain loosely bound SO 42- groups which are exchangable. Responsible for retardation of C 3A hydration (due to coating of C 3A).AF m - or monosulphate. Crystalline - layerstructure derived from that of Ca(OH)2 by theordered replacement of one Ca 2+ ion in threewith Al 3+ or Fe 3+. These layers alternate withones containing anions which balance thecharge (e.g. SO 42-, OH -, etc.) and H 2O.Composition is [Ca 2(Al,Fe)(OH)6].X.x H 2O,where X represents the interlayer anion. Hydrogarnet - nominally C 3AH 6, but inpractice contains Fe and Si. Related to themineral grossular or garnet (Ca 3Al 2Si 3O 12)which has a cubic structure. Not normally aproduct of modern OPC hydration althoughpresent in blended cements and older Portland cements. Aqueous phase and pore structure - porefluid permeates the microstructure of the hardened cement paste via the pore system. It is highly alkaline (pH > 13) due to rapid and almost quantitative dissolution of Na and K salts from the cement clinker. The porosity of the paste comprises of interconnected and isolated pores, the pore sizes of which are important to the strength and dimensional stability of cement products.The CaO-SiO 2-H 2O systemCrystal structure of ettringiteCement Types and Standards : provides some quality restrictions to cement compositions and performance. Different types of cement are used to meet different performance criteria. Properties can be estimated from compositions and fineness. Try toestimate which cement types will be rapid hardening, low heat ouput or sulphate resistant Portland cements. Blended Cements The use of cements in concrete which have not been blended with some form of reactive additive will become less likely in the future. There are now a range of additives commonly used to enhance the properties of concretes and, in some cases, result in reduced materials costs. This is mainly because they are industrial by-products. The most common of these are: pulverised fly ash (PFA)- a coal combustion product; blastfurnace slag (BFS), from iron making, and; condensed silica fume (CSF) from the ferrosilicon industry. The suitabilityof such materials depends on: theirreactivity, their cost (availability) andtheir influence on the properties of theresulting concrete. All influence theinternal chemistry of the cementsystem, i.e. pH, mineral balances, andtheir generally slower reaction leadsto a longer equilibration time asreaction products of the additive re-equilibrate with cement hydrationproducts. Reactivity , in all cases,depends on glass content, particlesize, composition (nature ofimpurities) and external influencessuch as temperature, humidity andhydrating liquid composition. Silica fume: quartz reduced in an electric arc furnace - some SiO volatilisation and oxidation produces largely glassy SiO 2 particles of ≈100 nm diameter. Low density material with 86-95% reactive SiO 2.PFA : arises as a dust in chimney stacks above coal-burning power station furnaces. Have widely variable compositions depending on furnace operating conditions and coal source. Particle sizes may be low, with 50% < 10 μm or coarse with 50% < 40 μm. Particles are generally spherical (formed by rapid cooling from a melt) and may be hollow Composition (wt%) and Properties ofRelative compositions of common blending agents for Portland cements(cenospheres) with or without spheres inside (plerospheres). Largely glassy (85 - 90%) with small crystallites of mullite (A3S2) and quartz.BFS: produced in the iron blastfurnace. Fluxes impurity oxides and sulphides. Composition is monitored (defines iron quality). Best for iron maker when ∑(CaO+MgO)/∑(SiO2+Al2O3) is maximised. Mainly glassy (>95%) and has its own CaOcontent (approx. 40%).Hydration characteristics Silicafume reacts relatively fast in thecement system. Pastes require ahigher water content than silicafume-free ones unless asuperplasticiser is added. The silicais consumed in reaction withCa(OH)2and lime-rich C-S-Hresulting in a paste with lower (orno) Ca(OH)2and a C-S-H of low Influence of pfa addition on Ca(OH)2 contentCaO:SiO2ratio (maybe as low as 1.2). The nature of the CSF-cement reaction process leads to efficient pore-filling and consequent enhancement of mechanical performance (low porosity pastes are stronger than high porosity ones). Silica fume-OPC blends are therefore used in the production of High Strength Concrete (HSC) with compressive strengths routinely in excess of 100 MPa. PFA displays the same pozzolanic action as CSF (see plot above) but is generally much slower in reactivity due to the coarser particle size. Also, the alumina (around 30%) and iron (around 10%) content contribute to the formation of products other than C-S-H but even so, general C/S ratios can be significantly lower in PFA-OPC blends than in neat OPC. (Note that in all blended cements, compositional gradients are common.) Other products include hydrogarnet, e.g. C12A3FS4H16 was reported within a PFA cenosphere found in an aged paste (Rogers and Groves, Adv. Cements Research, 1, 841, (1988)). BFS has different hydration characteristics to CSF and PFA. Having a CaO content of its own, it is not a pozzolan as such (i.e. it does not depend on external sources of CaO to activate it - although its reactivity is accelerated by activators such as Ca(OH)2, Na2CO3, NaOH, etc). Typically, BFS exhibits an initial burst of activity in OPC-BFS blends. This is followed by a relatively dormant period which may last six months or more, depending on temperature, particle size and aqueous phase composition, before continued hydration consumes remaining glassy grains. Hydrotalcite (a magnesium aluminate hydroxide hydrate) and gehlenite hydrate (C2ASH8) are commonly found in BFS-OPC pastes along with ettringite, monosulphate and C-S-H but again, Ca(OH)2contents are substantially reduced and C-S-H has lower Ca/Si ratios with respect to neat OPC. A unique characteristic of BFS is its electrochemically reducing characteristics. E h values of < -500 mV vs SHE (standard hydrogen electrode) have been measured in pore fluids extracted from blends of 85% BFS - 15% OPC cured for 28 days. This compares with around +100 mV measured for equivalent OPC pastes. This feature has important implications for the use of BFS blends in waste immobilisation and for passivation mechanisms for steel.Effects of Blending Agents on Paste Microstructures. The durability of cement pastes is strongly influenced by: (i) internal chemistry, and (ii) paste microstructure. The industrial by-product additives above all influence the development of paste microstructures. In neat OPC pastes, two types of porosity contribute to the total pore volume. Isolated pores are completely enclosed by hydration products so that material transport into and out of the pore is limited. Connected porosity is that through which a continuous pathway betweenregions of the microstructureexists. Continuous orinterconnected porosity often(although not always) links theinterior of the paste to the outsideworld so that aggressive chemicalspecies can penetrate and degradethe paste internally havingconsequences for paste durability.The effect of the blending agentsidentified above on microstructureis to cause a reduction in thedegree of interconnected porosity.This is especially true in the caseof BFS-containing pastes.Although the overall porosity, asdetermined by neutron scatterring Microstructure in BFS-OPC blendsis still significant, the interconnected porosity as measured by intrusion methods (e.g. MIP) is low. DURABILITY- the ability of the product to resist changes imposed by its service environment. Durability includes influences of mechanical damage, e.g. abrasion, thermal expansion, but is more commonly associated with chemical effects, e.g. sulphate attack, chloride-induced or general corrosion of steel reinforcement, alkali-aggregate reaction, etc.Sulphate attack: - expansion arising from the reaction between monosulphate (4CaO.Al2O3.SO3.12H2O) and SO42- in the presence of aqueous Ca2+ to give ettringite. The conversion from the high density phase to the low density one can cause expansion and cracking. The cracking opens up new connected porosity which accelerates the transport of sulphate into the cement paste and the deterioration of the paste. (Try writing out the equations for the monosulphate-ettringite conversion).Delayed Ettringite Formation: - a fairly recently discovered problem relating to degradation in steam-cured products. A number of mechanisms for this have been proposed (and at least one major legal conflict has arisen based on assigning liability for failed concrete products). It is proposed that the temperature cycle used in steam-curing produces a non-crystalline ettringite precursor which, on cooling and after some extended time period, crystallises having absorbed the required amount of moisture. Carbonation: - lowering of matrix pH due to the reaction between dissolved CO2 and the calcerous phases in the paste. Found at surfaces, a zone of carbonated product penetrates towards the interior to a distance which is defined by the porosity of the paste.Carbonation can ultimately consume Ca(OH)2and C-S-H, the degradation of C-S-H leading to a progressive decalcification to very low Ca/Si ratios and ultimately, silica gel. Degradation of the principal binding phase therefore can lead to strength loss. A more immediate concern is the loss of high pH in the vicinity of steel reinforcement. A pH of greater than about 10.5 is thought to preserve a passive film on the steel, protecting it from corrosion. Loss of pH therefore increases the corrosion risk. Engineers specify a minimum ‘cover depth’ to attempt to deal with this problem but again, the depth of penetration is porosity dependent.Effect of Chloride: - used to be a common additive to cements to accelerate setting but this use is now banned in structural concretes (Why do you think CaCl2would accelerated cement setting?). Chloride interactions with set concrete are however common, e.g. de-icing salts, salt spray, etc. Penetration is via connected porosity so that cover concrete may quickly become heavily loaded with soluble chloride. Steel passivation films are rapidly de-stabilised by chloride locally giving rise to pitting corrosion and rapid deterioration of the steel (the corrosion is focused in series of a small areas). There are competing influences of alkalinity and chloride effects so that a useful parameter to monitor is the [Cl]/[OH] ratio.Steel Reinforcement Corrosion: The oxidation of Fe(m) to Fe2+. In addition, further oxidation and cathodic reactions lead to production of oxides and oxyhydroxides of Fe (III) which produces a low permeability ‘passive’ film which slows the corrosion rate down considerably. Where corrosion can continue (by depassivation), expansion of corrosion products at the cement-steel interface and the subsequent spalling of cover concrete can occur. Many examples of this can be seen in concrete structures. Spalling leads to exposure of previously internal concrete as a fresh site for environmental damage.Alkali -Aggregate Reaction (AAR): Certain rocks contain silica in a mildly reactive form. Generally, flints, opals, cherts and strained quartz have a high degree of reactivity in concretes. The reaction is driven by the high pH pore fluid and the reactive silica and gives rise to a sodium silicate gel product which contains only a small amount of calcium. The gel imbibes water causing swelling and this gives rise to expansion cracks in affected concretes. The degree of expansion is important with respect to the servicability of affected structures. A recent study on a water inlet tower of a dam in Tasmania, Australia, showed that AAR expansion had increased the diameter of the tower sufficiently so that the inlet valves were unable to stem the flow of water when they were in the closed position.Glass-fibre Reinforcement Corrosion: Unlike steel reinforcement, glass fibres are introduced in random orientation and throughout the paste. Typically, as filament bundles (of around 50 filaments) the fibres will be of variable length (up to 2 cm typically). As in the AAR, the highly alkaline cement pore fluid attacks the siliceous glass to produce a gel which imbibes water. The result is loss of effective fibre diameter as the gel continues to form. Occasionally, Ca(OH)2 crystals attach themselves to the fibre and degrade the fibre locally (notching) but the more general attack occurs even when pozzolans are added to minimise notching. This degrading reaction prohibits the use of glass reinforced concrete (GRC) as sole reinforcement in structural concrete.。
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Porosity, pore size distribution and in situ strength of concreteRakesh Kumara, B. Bhattacharjeeb,*aBridges Division, Central Road Research Institute, New Delhi 110 020, IndiabDepartment of Civil Engineering, Indian Institute of Technology-Delhi, Hauz Khas, New Delhi 110 016, India
Received 23 July 1997; accepted 24 July 2002
AbstractIn this study, in situ strength of concrete was determined through compression test of cores drilled out from laboratory cast beams. Theapparent porosity and pore size distribution of the same concrete were determined through mercury intrusion porosimetry, performed onsmall-drilled cores. The normal-strength concrete mixes used in the experimental investigation were designed to exhibit a wide variation intheir strengths. To ensure further variation in porosity, pore size distribution and strength, two modes of compaction, two varieties of coarseaggregates, different levels of age, curing period and exposure condition of concrete were also introduced in experimental scheme. With thedata so generated, an appraisal of the most frequently referred relationships involving strength, porosity and pore size of cement-basedmaterials was carried out. Finally, a new empirical model relating the in situ strength of concrete with porosity, pore size characteristics,cement content, aggregate type, exposure conditions, etc., is presented.
Keywords: Mercury porosimetry; Pore size distribution; Pore system; Concrete; Cement content
1. IntroductionConcrete prepared with hydraulic cement binder can beregarded as a chemically bonded ceramic. The hydrationreaction of cement results in a product consisting of solidand a pore system [1]. Pores are thus inherent to concrete.Pores in concrete can also result from inadequate compac-tion. This pore system governs the most important prop-erties of concrete, notably its strength [2,3]. Well-compactedconcrete prepared with hard low-porosity aggregates may beassumed to be a multiphase material consisting of coarseaggregates embedded in mortar matrix. The mortar matrixconsists of fine aggregates, the solid cement hydrates,unhydrated cement, etc., and the pore system [4]. The poresystem present in the mortar of concrete, however, ismarkedly different from the pores of well-compacted mortarprepared independently using identical proportions of therelevant ingredients. The above difference in the two poresystems is due to the transition zone pores present atmortar-aggregate interface [5-7]. Capillary porosity ofhardened cement paste depends on water-to-cement ratio.
Water-cement ratio also governs the transition zone por-osity in concrete [4]. Thus, there are a number of well-established strength versus water-cement ratio relation-ships, which indirectly relate the strength of concrete withits pore system characteristics [4,8,9]. These relationshipsserve their purpose very well in the design of concretemixes. A few of these relationships take into account aircontent and degree of hydration of concrete. However, suchindirect relationships do not take into account the porespresent in hardened concrete in structure due to inadequatecompaction, etc. Further, the pore system in concrete alsochanges with degree of hydration and chemical changes dueto aggressive environments, etc. A direct relationship, on theother hand, can facilitate the strength estimation of in situconcrete from the knowledge of its pore system character-istics. For the purpose of mix design, however, strength/water-cement ratio relationships are more useful. The mostimportant characteristics of pore system are porosity andpore size distribution, which can be determined throughmercury intrusion porosimetry (MIP). However, MIP resultsare affected by a number of factors and the same must besuitably accounted for in the experimental procedure adop-ted [10-14]. Secondly, the smallest size of pore, in whichmercury can intrude, depends upon the maximum intrusionpressure applied. Consequently, extent of porosity that can156R. Kumar, B. Bhattacharjee / Cement and Concrete Research 33 (2003) 155-164be determined by porosimetry test depends upon the natureof the pores, the size of the smallest pore likely to beencountered in the material and the maximum intrusionpressure applied.The pore system in cement-based materials consists offour types of pores. These are: (a) gel pores, which aremicropores of characteristic dimension 0.5-10 nm; (b)capillary pores, which are mesopores with average radiusranging from 5 to 5000 nm; (c) macropores due to deliber-ately entrained air; and (d) macropores due to inadequatecompaction. In concrete, in addition to the above pores,there can be cracks at aggregate-mortar interface due toshrinkage. The gel pores, which are mostly of 1.5-2.0 nmsize, do not influence the strength of concrete adverselythrough its porosity, although these pores are directly relatedto creep and shrinkage. Capillary pores and other largerpores, on the other hand, are responsible for reduction instrength and elasticity, etc. [4,7,15-17]. Thus, while dealingwith an empirical strength-porosity relationship of con-crete, contribution of the gel pores in the overall porosityand pore size distribution of concrete can be neglected,without introducing any significant error. Hence, to deter-mine the pore system characteristics influencing thestrength, the maximum pressure in the porosimetry testmust be sufficient to cause intrusion of mercury in thesmallest capillary pore. In mercury porosimetry, a majorpart of gel pores remains nonintruded. Further, the closedpores also remain nonintruded. One other limitation pointedout as regard to mercury porosimetry is that it measuresentry sizes rather than true pore size that is related to inkbottle effect [18]. Thus, the porosity determined, as above,is apparent porosity.A number of relationships relating strength of cement-based materials with their pore system characteristics areavailable in the literature. In this paper, firstly, the results ofan experimental investigation are presented, whereby dataon in situ cube compressive strength of concrete—estimatedthrough compression test of cores drilled out from labor-atory cast beams—are generated, together with MIP data forthe same concrete. This is followed by an appraisal wherebymost frequently referred relationships involving strengthand pore system characteristics of cement-based materialsare evaluated for their suitability in strength estimation of insitu concrete. Finally, a new empirical relationship for in situstrength of concrete is proposed, which takes apparentporosity, pore size characteristics (corresponding to 33,000psi intrusion pressure) and binder content of the concreteinto account.2. Experimental investigation2.1. Objectives and scopeThe main objectives of this experimental investigationwere to generate sufficient data on strength, apparentporosity and pore size distribution of concrete. It was alsodesired that the strength data so generated should adequatelycover the range of strength usually encountered for normal-strength concrete. High-strength concrete, produced usingwater-reducing agent and pozzolanic microfiller, was leftout of the scope of this work.