Impact toughness and microstructure relationship in niobium- and vanadium-microalloyed steels proces
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1.the Iron Age 铁器时代2.covalent bonding 共价键,共价结合posites 复合材料4.crystal lattice 晶体点阵,晶格position and structure 成分和结构6.tensile strength抗拉强度,抗张强度7.ferrous metals 黑色金属8.gray cast iron 灰口铸铁9.austennitic stainless 奥氏体不锈钢10.weldability and hardenability 可焊性和可淬性11.refractory metals 难溶金属11.carbide and nitride碳化物和氮化物12.stiffness 刚度13.corrosion 腐蚀14.the Bronze Age 铜器时代15.metallic bonding 金属键,金属结合16.polymers 高分子材料17.ceramics and glasses 陶瓷和玻璃18.elementaty cell 晶胞19.direction indices晶向指数20.synthesis and processing 合成和加工21.yeild strength 屈服强度22.nonferrous metals 有色金属23.white cast iron白口铸铁24.martensitic stainless steels 马氏体不锈钢25.castability and formability 铸造性能与模锻性能26.titanium and nickel钛和镍27.precious metals 贵金属28.oxide and sulfide氧化物和硫化物29.die cast alloy压铸合金30.elasticity 弹性,弹力31.brittleness脆性32.fatigue strength 疲劳强度33.corrosion腐蚀34.annealing 退火35.high compressive strength 高压缩强度材料工程materials engineering 金属及其化合物metals and their alloys 面心立方晶格face-centered cubic lattice 材料塑性the plasticity of materials 普碳钢plain-carbon steels 陶瓷ceramics 合金元素alloying elements 表面处理surface treatment 金属物理性能the physical property of metals 材料科学materials science 金属材料metallic materials 体心立方晶格body-centered cubic lattice 材料的强度the strength of materials 有色金属nonferrous metals 合金钢alloy steels 铝及铝合金aluminums and aluminum alloys 加工硬化work hardening 热处理heat treated 金属力学性能mechanical propertyAbsorbed energy吸收功transition temperature转变温度modulus of elasticity弹性模量conductivity导电性thermal expansion热膨胀heat capacity 热容mold铸型rolling轧制forming 模压thermosetting ploymers热固性材料thermoplastic ploymers 热塑性材料stress versus strain应力应变pig iron生铁wrought iron熟铁steel malking 炼钢smelting熔炼blast furnace鼓风炉castability可锻性machinability机加工性nonmachinable不可机加工的hardenability可淬硬性nonmagnetic非磁铁alloyed steels合金钢anneal退火stree-corrsion cracking应力腐蚀断裂high-strength low-alloy steel高强度低合金钢cast iron alloys铸铁合金heat-treatable 可热处理的solubility溶解度thermo-mechanical 热加工性plain-carbon steel普碳钢electrolytic iron电解铁Introduction to materials材料概论coordination nunber配位数polycrystals多晶体anisotropy各向异性hexagonal close-packed structure 密排六方结构impact strength冲击强度tensile strength拉伸强度yield point屈服点utimate strength极限强度breaking strength破坏强度fracture toughness断裂韧度thoughness 韧性elastic limit弹性极限creep strength蠕变强度creep蠕变fatigue life 疲劳寿命corrosion resistance抗腐蚀性wear-resistance 耐磨性wear rate磨损率oxidation resistance抗氧化性imperfection缺陷austenitic马氏体martensitic 马氏体pearlite珠光体ferritic铁素体iron carbide渗碳体stainless steel不锈钢fracture 断裂compouds化合物specific strength比强度allotropic同素异形体reractory metals耐火材料anodize阳极电镀forging锻造casting铸造hardness硬度gray cast iron灰口铸铁magnetin磁性rust铁锈ingots铸锭malleable cast iron 可锻铸铁brittle materials脆性材料white cast iron 白口铸铁gears齿轮shafts轴weldable可焊接的unweldable不可焊接的weldablility可焊接性tool steels工具钢metallic bonding金属键covalent bonding共价键ionic bonding离子键hydrogen bonding 氢键crystal lattice晶格crystalline晶体amorphous非晶体packing factor致密度crystallographic indices结晶指数slip planes滑移面close-packed planes密排面elasticity弹性Elongation rate延伸率stress-rupture properties应力开裂reduction in area断面收缩句子:1,It is generally the behavior of materials is which limits the performance of machines and equipment.材料的性能通常限制着机器和设备的性能2,It is useful to consider the extent of metallic behaverior in the currently known range of chemical elements.在目前已知的化学范围内考察其金属性的程度是很有用的3,The packing factor is determined as the ratio of the volume of all elementary particles per elementary cell to the total volume of the elementary cell.填充因子的大小取决于每个晶胞中所有基本微粒的体积之和与整个晶胞体积之间的比率4,In most materials more than one phase is present, with each phase having its unique atomic arrangement and properties. Control of the type, size, distribution, and amount of these phases within the main body of the material provides an additional way to control properties of a material.在大多数材料中,往往存在着不止一种相,每一种相都有其各自的原子排列和特性。
第51卷第10期2020年10月中南大学学报(自然科学版)Journal of Central South University (Science and Technology)V ol.51No.10Oct.2020TBM 滚刀刀圈材料合金成分对组织和耐磨性能的影响贾连辉1,尚勇1,龙伟民2,夏毅敏3,薛广记1(1.中铁工程装备集团有限公司,河南郑州,450016;2.郑州机械研究所有限公司,河南郑州,450001;3.中南大学机电工程学院,湖南长沙,410083)摘要:为提高TBM 滚刀刀圈在高磨蚀地层的使用寿命,研究刀圈合金成分和组织中耐磨相种类及状态对耐磨性的影响规律,调配新型TBM 刀圈材料进行微观组织观察,并通过磨粒磨损试验、缩尺滚刀破岩试验及掘进破岩试验进行磨损性能对比。
研究结果表明:C ,Cr 和Mo 等合金元素的增多有助于共晶碳化物耐磨相的形成,对材料的耐磨性有一定的提升作用,而对材料的抗冲击性却是不利的;耐磨相的尺寸和形貌对材料耐磨性能及硬度的影响各不相同,大块的共晶碳化物对耐磨性的贡献比粒状的共晶碳化物的高,大块的共晶碳化物对硬度的贡献比粒状的共晶碳化物的略小。
在掘进高磨蚀、完整性较好的弱冲击岩层时,相比于常规的高韧性C-1材料,C-2新材料的刀圈寿命可提升30%以上,C-3新材料的刀圈寿命可提升70%以上。
3种材料的综合性能能够满足不同岩层的掘进要求,可为刀圈地质适应性选型提供参考。
关键词:滚刀刀圈;合金成分;共晶碳化物;耐磨性能中图分类号:U455.31文献标志码:A开放科学(资源服务)标识码(OSID)文章编号:1672-7207(2020)10-2730-09Effect of alloy composition of materials for TBM cutter rings onmicrostructure and wear resistanceJIA Lianhui 1,SHANG Yong 1,LONG Weimin 2,XIA Yimin 3,XUE Guangji 1(1.China Railway Engineering Equipment Group Co.Ltd.,Zhengzhou 450016,China;2.Zhengzhou Research Institute of Machinery Mechanical Engineering Co.Ltd.,Zhengzhou 450001,China;3.School of Mechanical and Electrical Engineering,Central South University,Changsha 410083,China)Abstract:In order to improve the service life of disc cutter rings in TBM in high erosion lithology,the effects of alloy composition ingredient and type of wear-resistant phase in microstructure on wear resistance were studied.New TBM cutter ring material was blended for microstructure observation.The wear performance was compared through abrasive wear test,scale-reduction rock-breaking test and tunneling rock-breaking test.The results show that the increases of C,Cr,Mo and other alloying elements enhance the formation of wear-resistant phases of eutectic carbides,and have a certain effect on improving the wear resistance of the material,but reduce the impactDOI:10.11817/j.issn.1672-7207.2020.10.005收稿日期:2020−01−25;修回日期:2020−04−29基金项目(Foundation item):国家重点研发计划项目(2017YFB1302601);河南省重大科技专项(181200210100)(Project(2017YFB1302601)supported by the National Research and Development Program of China;Project(181200210100)supported by the Significant Science and Technology Program of Henan Province)通信作者:贾连辉,教授级高级工程师,从事隧道掘进机设计制造研究;E-mail:**********************第10期贾连辉,等:TBM滚刀刀圈材料合金成分对组织和耐磨性能的影响resistance of the material.The effect of the size and morphology of the wear-resistant phase on the wear resistance and hardness of the material is also rge eutectic carbides contribute more to wear resistance than the granular eutectic carbides,and large eutectic carbides contribute slightly less to the hardness than the granular eutectic carbides.In driving high abrasion and weak integrity rock formations,compared with the conventional high toughness C-1material,the life of the cutter ring of the new C-2material can be increased by more than30%, and C-3new material ring life can be increased by more than70%.The comprehensive performance of the three materials can meet the requirements of different rock formations,which provides reference for the geological adaptability selection of cutter ring.Key words:disc cutter ring;alloy composition;eutectic carbide;wear-resisting performance岩石隧道掘进机(tunnel boring machine,TBM)掘进过程中伴随刀盘转动,刀盘上安装的盘形滚刀刀圈直接与岩体相互作用,滚刀贯入岩体滚动挤压,岩石表面产生局部变形并出现微观裂纹,随着挤压力增大,微观裂纹发展成为主裂纹并贯通,形成岩片破碎[1−2]。
Journal of Materials Science and Engineering B 1 (2011) 636-640Formerly part of Journal of Materials Science and Engineering, ISSN 1934-8959Development of New Tool Steels for Forging DiesPavel Šuchmann1, Jiří Krejčík 2 and Ludvík Martínek31. COMTES FHT a.s., Průmyslová 995, 33441 Dobřany, Czech Republic2. SVÚM a.s., areál VÚ, Podnikatelská 565, 190 11 Praha 9, Běchovice, Czech Republic3. ŽĎAS a. s., Strojírenská 6, 591 71 Žďár nad Sázavou, Czech RepublicReceived: March 30, 2011 / Accepted: April 10, 2011 / Published: October 25, 2011.Abstract: Forging dies used for close dies forging of small and middle-sized steel parts are required to possess an optimum combination of strength, toughness, resistance to tempering and other properties. Typical alloying elements include chromium, vanadium, molybdenum, or tungsten. This alloying strategy can be found e.g. in the steels 1.2343, 1.2344 and others. The present paper describes new alloying concepts of steels for forging dies based on the 1.2343 steel. By increasing the carbon content, and in some cases increasing the tungsten level and adding niobium, using a sufficient metallurgical procedure and subsequent special process for ingot forging, the hardness, toughness and wear resistance of the steel have been enhanced significantly. The lifetime of dies made from the improved steels is about 50%-100% longer than that of dies made from conventional 1.2343 steel.Key words: Tool steel, metallurgy, forging die, lifetime.1. IntroductionManufacturers of small closed-die forgings have been for a long time greatly interested in affordable tool steels with a good strength-toughness ratio and with a precisely specified metallurgical processing procedure. Such steels are fit for rather versatile applications involving most types of forging dies. The steel 1.2343 which is one of the most widely used materials in forging plants across Europe is a typical representative of such tool material. However, it is often difficult to find such a supplier of this steel on the Czech market which guarantees the required chemical composition and homogeneous microstructure with very low inclusion content, uniform carbide distribution and other parameters which are decisive for end-use properties of forging dies.In recent years, companies ZDAS a.s. and in cooperation with forge VIVA ZLIN Comp., and research institutes SVÚM a.s. and COMTES FHT a.s. have been working intensively on optimizing theCorresponding author: Pavel Šuchmann, research fields: tool steels, forging, heat treatment, wear resistance. E-mail: ***************************.production of steel 1.2343 with the aim of achieving best possible properties while keeping competitive price. Another goal of the proposed research was to define internal technical standards for metallurgical quality of tool steels to be applied at ŽĎAS a.s. in orderto update widely used but dated Poldi standards [1]. Besides the development of metallurgical processing of this steel, several chemical composition variants have been proposed for making dies with high hardness and wear-resistance requirements.2. Manufacturing of Experimental Materials2.1 Quality RequirementsOn the basis of long-term requirements of tool steel buyers, the following fundamental quality specifications for tool steel forgings have been identified:y sulphur level of no more than 0.005 wt%, very low content of phosphorus and other undesirable residual elements;y non-metallic inclusion content (according to ASTM E45-97) should not exceed values listed inTable 1;All Rights Reserved.Development of New Tool Steels for Forging Dies637Table 1 Highest acceptable amount of non-metallic inclusions in the tool steel acc. to ASTM E45-97.InclusionsType Fine CoarseA (sulphides) 1.0 0.5B (aluminates) 1.5 1.0C (silicates) 1.0 1.0D (globular oxides) 2.0 1.0y prior austenite grain size of G = 8 or finer (according to ASTM E 112).In addition to these fundamental criteria, microsegregation, carbide distribution and other standard microstructure parameters were evaluated according to NADCA 207. 2.2 Method of ProductionExperimental ingots were processed in vacuum (VD process). One of the ingots was arc-remelted in VAR equipment prior to forging. The above quality specifications have also been met by the materialproduced by the VD process without remelting. Asexpected, the vacuum remelting improved the quality parameters (resulting in zero inclusion content). However, due to high cost of this process and unavailability of the VAR equipment in the ŽĎAS company, remelted ingots ceased to be used.In order to achieve optimum amount of forging reduction, all the above materials were deformed along three axes (involving both drawing out and upsetting) with the forging reduction of at least 4.3. Modification of the Chemical Composition of 1.2343 SteelWith regard to special parameters of the trial die used for tool steel testing (see section 5), several chemical composition variants have been proposed(Table 2), leading primarily to higher hardness and wear resistance. In the variant no. 1 of the 1.2343chemical composition, an addition of niobium wasused. Niobium’s ability to form carbides is often used both in structural [2, 3] and tool steels [4, 5]. In the variant no. 2, carbon and vanadium levels have been increased in addition to alloying with niobium. Thepurpose was to increase hardness and hardenability ofthe material. The variant 3 included higher carbon content and additions of tungsten and vanadium in comparison with the 1.2343 standard composition. 4. Analysis of Properties of Experimental MaterialSpecimens taken from experimental melts were heat treated to hardnesses of 53 (all specimens) and 55 and 57 HRC (only those with modified chemical compositions). Subsequently, impact toughness tests were carried out for longitudinal and transverse directions (relative to the axis of the bar forged from the initial ingot) and abrasive wear resistance tests. Their results are listed in Table 3, showing that modifying the chemical composition significantly improved the material’s hardenability (hardness above 53 HRC is not achievable in the conventional 1.2343 steel) and wear resistance. However, all modified variants have been found to have lower impact toughness, in particular in the direction perpendicular to the axis of the forged workpiece. In order to eliminate this, the ingot forging process will be optimized further.In addition to mechanical tests, an evaluation of microstructure according to specification described in 2.1 was carried out. All experimental materials satisfied all testing criteria. Minute inclusion contentTable 2 Chemical composition of tool steels investigated.MaterialChemical composition (wt%)C Si Cr Mn Mo V Nb W1.2343-standard 0.37 1.0 5.00 0.4 1.20 0.45 0.00 0.00 Variant 1 (Nb) 0.39 1.0 4.95 0.4 1.16 0.42 0.18 0.00 Variant 2 (Nb, C, V) 0.54 1.0 4.95 0.4 1.15 0.62 0.18 0.00 Variant 3 (W, V, C) 0.49 1.0 4.90 0.4 1.17 1.60 0.00 1.63 All Rights Reserved.Development of New Tool Steels for Forging Dies638Table 3 Mechanical properties of specimens made from experimental alloys (tests at room temper). Steel typeHardness HRCImpact toughness KCU (J/cm 2) Resistance to wear ψII ┴ 1.2343-standard 53 2320 1.69Variant 1 (Nb)53 23 16 1.83 55 16 11 1.93 57 12 7 2.06 Variant 2 (Nb, C, V)53 20 15 1.85 55 15 11 1.95 57 11 7 2.08 Variant 3 (W, C)53 21 15 1.82 55 15 10 1.89 57 11 6 2.0was achieved. The prior austenite grain size in all testedspecimens was between G 8 and 10. An example of microstructure of standard 1.2343 grade produced in the ŽĎAS company with visible prior austenite grainboundaries is shown in Fig. 1.Tempering curves were obtained for the variants with modified chemical compositions. They are shown in Figs. 2-4.Fig. 1 Microstructure of a 1.2343 tool steel with visible prior austenite grain boundaries (G = 8).4547495153555759480500520540560580600620Annealing temperature [°C]H R CFig. 2 Annealing curves-variant 1 (Nb).4547495153555759480500520540560580600620Annealing temperature [°C]H R CFig. 3 Annealing curves-variant 2 (Nb, C, V).47495153555759616365460480500520540560580600620Annealing temperature [°C]H R CFig. 4 Annealing curves-variant 3 (W, C).5. Testing of Forging DiesThe forging die shown in Fig. 5 is used in Kovárna VIVA Zlín for manufacturing small forgings (with the weight of about 1 kg). With regard to production of large series (up to 100 thousand pieces yearly over several years), the die is considered a suitable candidate for testing of new tool materials. Prior to this testing initiative, the die used to be made from standardAll Rights Reserved.Development of New Tool Steels for Forging Dies639Fig. 5 Forging die used for field tests and its worn surface.1.2343 steel quenched and tempered to 47 HRC and its life was equal to 4,500 strokes. The nature of its wear (Fig. 5, bottom) indicates that during its service, abrasive wear and local plastic deformation rather than cracking are the chief phenomena taking place in the die. For this reason, the die material was proposed to be treated to higher hardness.A series of tests was performed on dies from standard 1.2343 steel and from the above described modified materials conventionally treated to a hardness above 50 HRC. Forging conditions were kept stable in the course of testing. The life of dies was monitored. Results of selected tests are shown in Table 4. They indicate that higher hardness led to a significant improvement in the die life (by about 70%) even in the variants with no modification of chemical composition. Using steel with modified chemical composition and equal hardness extended the life of the die even more. Its life was almost 100% longer than that of the initial die.All chemical composition variants tested have proven to be beneficial in practice and can be considered usable for manufacturing forging dies.6. ConclusionsThe above results indicate that the development of a high-quality hot work tool steel with chemical composition based on that of 1.2343 was successful. The newly implemented quality standards containing requirements on both micropurity and grain size make the quality management of the steel producer more efficient. Furthermore, test pieces from steels with three different modified chemical compositions were made. The modifications led to higher hardenability and abrasive wear resistance. All investigated materials have been field-tested as forging die materials in Kovárna VIVA Zlín. Their utilization greatly extended the life of forging dies. Testing in the forging plant has also shown that in some cases the dies can be quenched and tempered to a hardness significantly higher than 50 HRC without causing in-service cracking.With regard to favourable results of the tests, all examined variants of the steel 1.2343 can be regarded as usable hot work tool steels. Since 2009, the above variants have been protected by utility designs.AcknowledgmentsThe presented results have been achieved with support of Ministry of Industry and Trade of the Czech Republic within the project TANDEM FT-TA 3/091.Table 4 Results of field tests of forging dies.Die material Relative position of workpiece axis anddie parting planeHardnessHRCLife(No. of strokes)1.2343 perpendicular 474.3041.2343 perpendicular 537.0801.2343 parallel 537.628Variant 1 (Nb) perpendicular 54 8.499Variant 2 (Nb, C, V) perpendicular 54 9.388Variant 3 (W, V, C) perpendicular 54 8.470Variant 3 (W, V, C) parallel 56 7.759All Rights Reserved.Development of New Tool Steels for Forging Dies 640References[1] E. Přibil, A. Engst, V. Eichler, J. Průcha, B. Esterka, J.Krejčík, Tool Steel Poldi and Their Use, I. Part Prague, 1986.[2] E.V. Pereloma, I.B. Timokhina, P.D. Hodgson,Transformation behaviour in thermomechanical processedC-Mn-Si steel with and without Nb, Materials Science andEngineering A 273-275 (1999) 448-452.[3] D. Hauserová, H. Jirková, B. Mašek, Investigation ofphase transformations in high-strength low-alloyed steel,in: Proceedings of the 20th International DAAAM Symposium Intelligent Manufacturing and Automation: Theory, Practice and Education 20 (1) (2009) 1897-1898, [4]L.A. Dobrzanski, A. Zarychta, M. Ligarski, High-speedsteels with addition of niobium or titanium, Journal of Materials Processing Technology 63 (1997) 531-541.[5]P. Novak, D. Vojtech, J. Serak, Pulsed-plasma nitriding ofa niobium-alloyed PM tool steel, Materials Science andEngineering A 393 (2005) 286-293.All Rights Reserved.。
材料专业英语常见词汇The saying "the more diligent, the more luckier you are" really should be my charm in2006.材料专业英语常见词汇一Structure 组织Ceramic 陶瓷Ductility 塑性Stiffness 刚度Grain 晶粒Phase 相Unit cell 单胞Bravais lattice 布拉菲点阵Stack 堆垛Crystal 晶体Metallic crystal structure 金属性晶体点阵 Non-directional 无方向性Face-centered cubic 面心立方Body-centered cubic体心立方 Hexagonal close-packed 密排六方 Copper 铜Aluminum 铝Chromium 铬 Tungsten 钨Crystallographic Plane晶面 Crystallographic direction 晶向 Property性质 Miller indices米勒指数 Lattice parameters 点阵参数Tetragonal 四方的Hexagonal 六方的Orthorhombic 正交的Rhombohedra 菱方的Monoclinic 单斜的Prism 棱镜 Cadmium 镉 Coordinate system 坐 Point defec点缺陷Lattice 点阵 Vacancy 空位Solidification 结晶Interstitial 间隙Substitution 置换Solid solution strengthening 固溶强化Diffusion 扩散Homogeneous 均匀的Diffusion Mechanisms 扩散机制Lattice distortion 点阵畸变Self-diffusion 自扩散Fick’s First Law 菲克第一定律 Unit time 单位时间Coefficient 系数Concentration gradient 浓度梯度Dislocations 位错Linear defect 线缺陷Screw dislocation 螺型位错Edge dislocation 刃型位错Vector 矢量Loop 环路Burgers’vector 柏氏矢量Perpendicular 垂直于Surface defect 面缺陷Grain boundary 晶界Twin boundary 晶界 Shear force 剪应力Deformation 变形Small or low angel grain boundary 小角度晶界Tilt boundary 倾斜晶界Supercooled 过冷的Solidification 凝固Ordering process 有序化过程Crystallinity 结晶度Microstructure 纤维组织Term 术语Phase Diagram 相图Equilibrium 平衡Melt 熔化Cast 浇注Crystallization 结晶Binary Isomorphous Systems 二元匀晶相图Soluble 溶解Phase Present 存在相Locate 确定Tie line 连接线Isotherm 等温线Concentration 浓度Intersection 交点The Lever Law 杠杆定律Binary Eutectic System 二元共晶相图Solvus Line 溶解线Invariant 恒定Isotherm 恒温线Cast Iron 铸铁Ferrite 珠光体Polymorphic transformation 多晶体转变Austenite 奥氏体Revert 回复Intermediate compound 中间化合物Cementite 渗碳体Vertical 垂线Nonmagnetic 无磁性的Solubility 溶解度Brittle 易脆的Eutectic 共晶Eutectoid invariant point 共析点Phase transformation 相变Allotropic 同素异形体Recrystallization 再结晶Metastable 亚稳的Martensitic transformation 马氏体转变Lamellae 薄片Simultaneously 同时存在Pearlite 珠光体Ductile 可塑的Mechanically 机械性能Hypo eutectoid 过共析的Particle 颗粒Matrix基体Proeutectoid 先共析Hypereutectoid 亚共析的Bainite 贝氏体Martensite 马氏体Linearity 线性的Stress-strain curve 应力-应变曲线Proportional limit 比例极限Tensile strength 抗拉强度Ductility 延展性Percent reduction in area 断面收缩率Hardness 硬度Modulus of Elasticity 弹性模量Tolerance 公差Rub 摩擦Wear 磨损Corrosion resistance 抗腐蚀性Aluminum 铝Zinc 锌Iron ore 铁矿Blast furnace 高炉Coke 焦炭Limestone 石灰石Slag 熔渣Pig iron 生铁Ladle 钢水包Silicon 硅Sulphur 硫Wrought 可锻的Graphite 石墨Flaky 片状Low-carbon steels 低碳钢Case hardening 表面硬化Medium-carbon steels 中碳钢Electrode 电极As a rule 通常Preheating 预热Quench 淬火Body-centered lattice 体心晶格Carbide 碳化物Hypereutectoid过共晶Chromium 铬Manganese 锰Molybdenum 钼Titanium 钛Cobalt 钴Tungsten 钨Vanadium 钒Pearlitic microstructure 珠光体组织Martensitic microstructure 马氏体组织Viscosity 粘性Wrought 锻造的Magnesium 镁Flake 片状Malleable 可锻的Nodular 球状Spheroidal 球状Superior property 优越性Galvanization 镀锌Versatile 通用的Battery grid 电极板Calcium 钙Tin 锡Toxicity 毒性Refractory 耐火的Platinum铂Polymer 聚合物Composite 混合物Erosive 腐蚀性Inert 惰性Thermo chemically 热化学Generator 发电机Flaw 缺陷Variability 易变的Annealing 退火Tempering回火Texture 织构Kinetic 动力学Peculiarity 特性Critical point 临界点Dispersity 弥散程度Spontaneous 自发的Inherent grain 本质晶粒Toughness 韧性Rupture 断裂Kinetic curve of transformation 转变动力学曲线Incubation period 孕育期Sorbite 索氏体Troostite 屈氏体Disperse 弥散的Granular 颗粒状Metallurgical 冶金学的Precipitation 析出Depletion 减少Quasi-eutectoid 伪共析Superposition 重叠Supersede 代替Dilatometric 膨胀Unstable 不稳定Supersaturate 使过饱和Tetragonality 正方度Shear 切变Displacement 位移Irreversible 不可逆的金属材料工程专业英语acid-base equilibrium酸碱平衡 acid-base indicator酸碱指示剂 acid bath酸槽 acidBessemerconverter 酸性转炉 acid brick酸性耐火砖 acid brittleness酸洗脆性、氢脆性 acid burden酸性炉料acid clay酸性粘土 acid cleaning同pickling酸洗 acid concentration酸浓度 acid converter酸性转炉 acid converter steel酸性转炉钢 acid content酸含量 acid corrosion酸腐蚀 acid deficient弱酸的、酸不足的 acid dip酸浸acid dip pickler沉浸式酸洗装置 aciddiptank酸液浸洗槽acid drain tank排酸槽acidless descaling无酸除鳞acid medium酸性介质acid mist酸雾acid-proof paint耐酸涂料漆acid-proof steel耐酸钢acid-resistant耐酸钢acid-resisting vessel耐酸槽acid strength酸浓度acid supply pump供酸泵acid wash酸洗acid value酸值acid wash solution酸洗液acieration渗碳、增碳Acm point Acm转变点渗碳体析出温度acorn nut螺母、螺帽acoustic absorption coefficient声吸收系数acoustic susceptance声纳actifier再生器action line作用线action spot作用点activated atom激活原子activated bath活化槽activated carbon活性碳activating treatment活化处理active corrosion活性腐蚀、强烈腐蚀active area有效面积active power有功功率、有效功率active product放射性产物active resistance有效电阻、纯电阻active roll gap轧辊的有效或工作开口度active state活性状态active surface有效表面activity coefficient激活系数、活度系数actual diameter钢丝绳实际直径actual efficiency实际效率actual error实际误差actual time实时actual working stress实际加工应力actuating device调节装置、传动装置、起动装置actuating lever驱动杆、起动杆actuating mechanism 动作机构、执行机构actuating motor驱动电动机、伺服电动机actuating pressure作用压力actuation shaft起动轴actuator调节器、传动装置、执行机构acute angle锐角adaptive feed back control自适应反馈控制adaptive optimization自适应最优化adaptor接头、接合器、连结装置、转接器、附件材料科学基础专业词汇:第一章晶体结构原子质量单位 Atomic mass unit amu 原子数 Atomic number 原子量 Atomic weight波尔原子模型 Bohr atomic model 键能 Bonding energy 库仑力 Coulombic force共价键 Covalent bond 分子的构型 molecular configuration电子构型electronic configuration 负电的 Electronegative 正电的 Electropositive基态 Ground state 氢键 Hydrogen bond 离子键 Ionic bond 同位素 Isotope金属键 Metallic bond 摩尔 Mole 分子 Molecule 泡利不相容原理 Pauli exclusion principle 元素周期表 Periodic table 原子 atom 分子 molecule 分子量 molecule weight极性分子 Polar molecule 量子数 quantum number 价电子 valence electron范德华键 van der waals bond 电子轨道 electron orbitals 点群 point group对称要素 symmetry elements 各向异性 anisotropy 原子堆积因数 atomic packing factorAPF 体心立方结构 body-centered cubic BCC 面心立方结构 face-centered cubic FCC布拉格定律bragg’s law 配位数 coordination number 晶体结构 crystal structure晶系 crystal system 晶体的 crystalline 衍射 diffraction 中子衍射 neutron diffraction电子衍射 electron diffraction 晶界 grain boundary 六方密堆积 hexagonal close-packed HCP 鲍林规则 Paulin g’s rules NaCl型结构 NaCl-type structureCsCl型结构Caesium Chloride structure 闪锌矿型结构 Blende-type structure纤锌矿型结构 Wurtzite structure 金红石型结构 Rutile structure萤石型结构 Fluorite structure 钙钛矿型结构 Perovskite-type structure尖晶石型结构 Spinel-type structure 硅酸盐结构 Structure of silicates岛状结构 Island structure 链状结构 Chain structure 层状结构 Layer structure架状结构 Framework structure 滑石 talc 叶蜡石 pyrophyllite 高岭石 kaolinite石英 quartz 长石 feldspar 美橄榄石 forsterite 各向同性的 isotropic各向异性的 anisotropy 晶格 lattice 晶格参数 lattice parameters 密勒指数 miller indices 非结晶的 noncrystalline多晶的 polycrystalline 多晶形 polymorphism 单晶single crystal 晶胞 unit cell电位 electron states化合价 valence 电子 electrons 共价键 covalent bonding金属键 metallic bonding 离子键Ionic bonding 极性分子 polar molecules原子面密度 atomic planar density 衍射角 diffraction angle 合金 alloy粒度,晶粒大小 grain size 显微结构 microstructure 显微照相 photomicrograph扫描电子显微镜 scanning electron microscope SEM透射电子显微镜 transmission electron microscope TEM 重量百分数 weight percent四方的 tetragonal 单斜的monoclinic 配位数 coordination number材料科学基础专业词汇:第二章晶体结构缺陷缺陷 defect, imperfection 点缺陷 point defect 线缺陷 line defect, dislocation面缺陷 interface defect 体缺陷 volume defect 位错排列 dislocation arrangement位错线 dislocation line 刃位错 edge dislocation 螺位错 screw dislocation混合位错 mixed dislocation 晶界 grain boundaries 大角度晶界 high-angle grain boundaries 小角度晶界 tilt boundary, 孪晶界 twin boundaries 位错阵列 dislocation array位错气团 dislocation atmosphere 位错轴dislocation axis 位错胞 dislocation cell位错爬移 dislocation climb 位错聚结 dislocation coalescence 位错滑移 dislocation slip位错核心能量 dislocation core energy 位错裂纹 dislocation crack位错阻尼 dislocation damping 位错密度 dislocation density原子错位 substitution of a wrong atom 间隙原子 interstitial atom晶格空位 vacant lattice sites 间隙位置 interstitial sites 杂质 impurities弗伦克尔缺陷 Frenkel disorder 肖脱基缺陷 Schottky disorder 主晶相 the host lattice错位原子 misplaced atoms 缔合中心 Associated Centers. 自由电子 Free Electrons电子空穴Electron Holes 伯格斯矢量 Burgers 克罗各-明克符号 Kroger Vink notation中性原子 neutral atom材料科学基础专业词汇:第二章晶体结构缺陷-固溶体固溶体 solid solution 固溶度 solid solubility 化合物 compound间隙固溶体 interstitial solid solution 置换固溶体 substitutional solid solution金属间化合物 intermetallics 不混溶固溶体 immiscible solid solution转熔型固溶体 peritectic solid solution 有序固溶体 ordered solid solution无序固溶体 disordered solid solution 固溶强化 solid solution strengthening取代型固溶体 Substitutional solid solutions 过饱和固溶体 supersaturated solid solution非化学计量化合物 Nonstoichiometric compound材料科学基础专业词汇:第三章熔体结构熔体结构 structure of melt过冷液体 supercooling melt 玻璃态 vitreous state软化温度 softening temperature 粘度 viscosity 表面张力 Surface tension介稳态过渡相 metastable phase 组织 constitution 淬火 quenching退火的 softened 玻璃分相 phase separation in glasses 体积收缩 volume shrinkage材料科学基础专业词汇:第四章固体的表面与界面表面 surface 界面 interface 同相界面 homophase boundary异相界面 heterophase boundary 晶界 grain boundary 表面能 surface energy小角度晶界 low angle grain boundary 大角度晶界 high angle grain boundary共格孪晶界 coherent twin boundary 晶界迁移 grain boundary migration错配度 mismatch 驰豫 relaxation 重构 reconstuction 表面吸附 surface adsorption表面能 surface energy 倾转晶界 titlt grain boundary 扭转晶界 twist grain boundary倒易密度 reciprocal density 共格界面 coherent boundary 半共格界面 semi-coherent boundary 非共格界面 noncoherent boundary 界面能 interfacial free energy应变能 strain energy 晶体学取向关系 crystallographic orientation惯习面habit plane材料科学基础专业词汇:第五章相图相图 phase diagrams 相 phase 组分 component 组元 compoonent相律 Phase rule 投影图 Projection drawing 浓度三角形 Concentration triangle冷却曲线 Cooling curve 成分 composition 自由度 freedom相平衡 phase equilibrium 化学势 chemical potential 热力学 thermodynamics相律 phase rule 吉布斯相律 Gibbs phase rule 自由能 free energy吉布斯自由能 Gibbs free energy 吉布斯混合能 Gibbs energy of mixing吉布斯熵 Gibbs entropy 吉布斯函数 Gibbs function 热力学函数 thermodynamics function 热分析 thermal analysis 过冷 supercooling 过冷度 degree of supercooling杠杆定律 lever rule 相界 phase boundary 相界线 phase boundary line相界交联 phase boundary crosslinking 共轭线 conjugate lines相界有限交联 phase boundary crosslinking 相界反应 phase boundary reaction相变 phase change 相组成 phase composition 共格相 phase-coherent金相相组织 phase constentuent 相衬 phase contrast 相衬显微镜 phase contrast microscope 相衬显微术 phase contrast microscopy 相分布 phase distribution相平衡常数 phase equilibrium constant 相平衡图 phase equilibrium diagram相变滞后 phase transition lag 相分离 phase segregation 相序 phase order相稳定性 phase stability 相态 phase state 相稳定区 phase stabile range相变温度 phase transition temperature 相变压力 phase transition pressure同质多晶转变 polymorphic transformation 同素异晶转变 allotropic transformation相平衡条件 phase equilibrium conditions 显微结构 microstructures 低共熔体 eutectoid不混溶性 immiscibility材料科学基础专业词汇:第六章扩散活化能 activation energy 扩散通量 diffusion flux 浓度梯度 concentration gradient菲克第一定律Fick’s first law 菲克第二定律Fick’s second law 相关因子 correlation factor 稳态扩散 steady state diffusion 非稳态扩散 nonsteady-state diffusion扩散系数 diffusion coefficient 跳动几率 jump frequency填隙机制 interstitalcy mechanism 晶界扩散 grain boundary diffusion短路扩散 short-circuit diffusion 上坡扩散 uphill diffusion 下坡扩散 Downhill diffusion互扩散系数 Mutual diffusion 渗碳剂 carburizing 浓度梯度 concentration gradient浓度分布曲线 concentration profile 扩散流量 diffusion flux 驱动力 driving force间隙扩散 interstitial diffusion 自扩散 self-diffusion 表面扩散 surface diffusion空位扩散 vacancy diffusion 扩散偶 diffusion couple 扩散方程 diffusion equation扩散机理 diffusion mechanism 扩散特性 diffusion property 无规行走 Random walk达肯方程 Dark equation 柯肯达尔效应 Kirkendall equation本征热缺陷 Intrinsic thermal defect 本征扩散系数 Intrinsic diffusion coefficient离子电导率 Ion-conductivity 空位机制 Vacancy concentration材料科学基础专业词汇:第七章相变过冷 supercooling 过冷度 degree of supercooling 晶核 nucleus 形核 nucleation形核功 nucleation energy 晶体长大 crystal growth 均匀形核 homogeneous nucleation非均匀形核 heterogeneous nucleation 形核率 nucleation rate 长大速率 growth rate热力学函数 thermodynamics function 临界晶核 critical nucleus临界晶核半径 critical nucleus radius 枝晶偏析 dendritic segregation局部平衡 localized equilibrium 平衡分配系数 equilibrium distributioncoefficient有效分配系数 effective distribution coefficient 成分过冷 constitutional supercooling引领领先相 leading phase 共晶组织 eutectic structure 层状共晶体 lamellar eutectic伪共晶 pseudoeutectic 离异共晶 divorsed eutectic 表面等轴晶区 chill zone柱状晶区 columnar zone 中心等轴晶区 equiaxed crystal zone定向凝固 unidirectional solidification 急冷技术 splatcooling 区域提纯 zone refining单晶提拉法 Czochralski method 晶界形核 boundary nucleation位错形核 dislocation nucleation 晶核长大 nuclei growth斯宾那多分解 spinodal decomposition 有序无序转变 disordered-order transition马氏体相变 martensite phase transformation 马氏体 martensite材料科学基础专业词汇:第八、九章固相反应和烧结固相反应 solid state reaction 烧结 sintering 烧成 fire 合金 alloy 再结晶 Recrystallization 二次再结晶 Secondary recrystallization 成核 nucleation 结晶 crystallization子晶,雏晶 matted crystal 耔晶取向 seed orientation 异质核化 heterogeneous nucleation均匀化热处理 homogenization heat treatment 铁碳合金 iron-carbon alloy渗碳体 cementite 铁素体 ferrite 奥氏体austenite 共晶反应 eutectic reaction 固溶处理 solution heat treatment。
W机械工程材料IX)I : 10.11973/jxgccl202101006焊前和焊后调质处理下25C r 2N i 4M o V 钢焊接接头的组织及性能张敏,仝雄伟,李洁,许帅,贾芳(西安理工大学材料科学与工程学院,西安710048)摘要:对比研究了焊前和焊后调质处理条件下25C r 2N i 4M o V 钢焊接接头的显微组织、力学 性能和耐腐蚀性能,调质处理工艺为920 °CX1 h 油淬+580 °C X 2 h 回火,焊接工艺为手工焊条电 弧焊。
结果表明:焊前调质处理的接头焊缝组织为板条马氏体+S-铁素体+ M 23C S 碳化物,焊后调 质处理使焊缝中的S-铁素体溶解,形成了板条马氏体+回火索氏体+M 23C S 碳化物;焊后调质处理 条件下,焊缝中的板条马氏体细小均匀,M 23C 6碳化物呈颗粒状分布于原奥氏体晶界和马氏体板条 晶界处,焊缝的强度、冲击初性和耐腐蚀性能均优于焊前调质处理的。
关键词:25C r 2N i 4M o V 钢;焊缝;调质;显微组织;力学性能;耐腐蚀性能中图分类号:TG444文献标志码:A文章编号:1000-3738(2021)01-0034-07Microstructure and Properties of 25Cr2Ni4MoV Steel Welded Joint underPre-welding and Post-welding Quenching and Tempering TreatmentZHANG Min, TONG Xiongwei, LI Jie. XU Shuai. JIA Fang(School of Materials Science and Engineering ,Xi’an University of Technology, Xi’an 710048,China)Abstract : M icrostructure, mechanical properties and corrosion resistance of 25Cr2Ni4M oV steel welded jointwere compared and studied under conditions of pre-welding and post-welding quenching and tem pering treatm ents.T he quenching and tem pering proceSvS was oil quenching at 920 °C for 1 h and tem pering at 580 °C for 2 h. The welding process was manual electrode arc welding. The results show that by pre-welding quenching and tem pering, the m icrostructure of the joint weld zone consisted of lath m artensite» netw ork S-ferrite and M 23C 6 carbide. A fter the post-welding quenching and tem pering,the 5-ferrite in the weld was dissolved, and the lath m artensite, tem pered sorbite and M 23C 6 carbide were formed. U nder the post-welding quenching and tem pering condition, the lath m artensite in the weld was small and uniform , and the M 23C 6 carbide distributed in granular shapes on original austenite grain boundaries and m artensite lath grain boundaries ; the strength, impact toughness and corrosion resistance were better than those by the pre-welding quenching and tem pering treatm ent.Key words : 25Cr2Ni4M oV steel ; weld zone ; quenching and tem pering ; m icrostructure ; mechanicalproperties ; corrosion resistance25Cr2Ni4M〇V 钢中马氏体的形成,但若奥氏体化温 度过高,得到的板条马氏体较粗大[1]。
316L不锈钢薄板脉冲激光焊工艺参数及接头组织特征阎小军, 杨大智, 刘黎明(大连理工大学材料工程系,大连 116024)摘 要:研究了0.1mm316L不锈钢薄板脉冲激光焊工艺参数特征,分析了接头的组织和力学性能。
结果表明:0.1mm316L不锈钢薄板脉冲激光焊时适宜用小电流、大脉宽、高速度、高频率;焊缝中心为细小的等轴晶,边缘是细小的柱状晶;焊接接头的抗拉强度可达到母材的95%,伸长率可达到母材的85%。
关键词:不锈钢薄板;脉冲激光焊;工艺参数;组织特征中图分类号:TG456.7 文献标识码:A 文章编号:0253-360X(2004)03-121-03阎小军0 序 言316L不锈钢因其良好的力学性能,低廉的价格,已经成为最常用的医用金属材料。
目前广泛用于人工关节、骨折接合用夹板、人工心脏瓣膜等植入假体的制作。
在介入医疗器械中经常用到316L不锈钢薄板和细丝,例如经皮穿刺介入冠状动脉成形手术中用到的导丝和支架。
人们对316L不锈钢的研究方兴未艾,但研究的重点多集中在316L不锈钢的耐蚀性和生物相容性以及表面改性对其耐蚀性和生物相容性的影响上,而对其焊接加工工艺及焊缝组织的性能研究很少。
脉冲激光焊作为一种精密的连接方法,在医疗器械的制造中发挥着很大的作用。
YAG脉冲激光在焊接金属过程中由于光辐射的高峰值功率、间断作用的特性,作用过程显示出物态动态变化的特点;又由于焊接工艺控制因素较多,稳定的焊接质量对工艺规范要求极为严格[1]。
这一点在薄板的焊接过程中体现得尤为突出。
奥氏体不锈钢导热系数小、线膨胀系数大、焊接过程中由热收缩而引起的工件横向位移、连接时对接缝间隙过大或过小等原因,难以保证焊接质量,对接焊中最易产生的缺陷是烧穿。
激光焊时在焊缝起焊和收尾处均易出现半椭圆形缺口[2],这些都与脉冲激光焊接时的工艺参数配合是否合理有关,而针对这方面的研究报道却较少。
文中探索了0.1mm316L不锈钢薄板脉冲激光焊的最佳工艺参数配合,分析了焊接接头的组织特征和力学性能。
时效处理对7050锻造铝合金微观组织及性能的影响陈烨; 刘志义; 赵娟刚; 刘冠华【期刊名称】《《矿冶工程》》【年(卷),期】2019(039)005【总页数】5页(P129-132,143)【关键词】时效处理; 7050锻造铝合金; 微观组织; 回归再时效; 自然时效; 力学性能; 腐蚀性能【作者】陈烨; 刘志义; 赵娟刚; 刘冠华【作者单位】中南大学材料科学与工程学院湖南长沙410083【正文语种】中文【中图分类】TG156Al-Zn-Mg-Cu 合金强度高、密度小,作为结构材料被广泛应用于航空和高速列车等领域[1-3]。
作为可热处理强化合金,时效处理是提高合金综合性能的主要手段。
通过T6 处理,合金能达到较高的强度,但缺点是抗腐蚀性能差;而过时效(T7X)态合金抗腐蚀性好,但拉伸强度下降。
RRA 处理[4]能克服以上2 种时效处理的缺陷,该时效态合金晶内析出相为GP 区和细小η′颗粒,晶界为粗大的断续分布的η 相,因而合金具有较高的强度和低的腐蚀敏感性[5]。
本文在前人热处理工艺的研究[5-7]基础上,通过降低回归温度、延长时间优化传统RRA 制度,探讨了不同时效处理对合金的力学性能及腐蚀性能的影响。
1 实验本实验所用材料为7050 锻造铝合金,其化学成分见表1。
实验样品均由线切割机从锻件上沿垂直于锻造方向切取,在空气炉中进行470 ℃/1 h+477 ℃/3 h双级固溶处理后淬火。
将固溶后的试样进行3 种不同时效处理:T74、RRA、四级时效,工艺参数见表2,其中四级时效与RRA 之间的差异在于前者在回归和再时效处理之间增加了一段24 h 自然时效(NA)。
表1 7050 锻造铝合金化学成分(质量分数)/%?表2 时效工艺参数?室温拉伸性能在CSS 44100 试验机下进行,加载速率为2 mm/min,温度为室温。
利用Tencnai-G220透射电镜(TEM)观察不同状态试样的微观组织,加速电压200 kV。
建筑材料单词carbonating 碳化处理carbon steel 碳素钢carbonated shrinkage 碳化收缩carbon tetrachloride 四氯化碳cation 阳离子 anion 阴离子cationic emulsifier 阳离子乳液化剂capillary voids (pores) in cement水泥中的毛细管capillary water 毛细管水carbon dioxide 二氧化碳cement 水泥cement clinker 水泥熟料cement fineness 水泥细度cement mortar 水泥砂浆cement resistance to chemical水泥抗化学侵蚀性cement paste 水泥浆cement soundness 水泥安定性cement specifications 水泥规范cement strength 水泥强度cement types 水泥品种cement-water ratio 灰水比characteristic strength 特征强度chemically combined water 化学结合水crack 裂纹chemical property 化学性质chert 燧石 ( 黑硅石 )chloride 氯化物chord modulus of elasticity 弦弹性模量civil Engineering 土木工程clinker 熟料coarse aggregate 粗集料coefficient of permeability of concrete 混凝土渗透系数coefficient of thermal expansion热膨胀系数coefficient of shrinkage 收缩系数coefficient of shrinkage of concrete 混凝土收缩系数compacting factor test 捣实系数试验compaction (consolidation)捣实( 捣固 ) compressive strength 抗压强度computer control system 计算机控制系统cube size 立方体试件尺寸coarse aggregate ratio to fine粗集料与细集料之比composite insulation 复合绝热层component组分 , 成分 , 构件composite 复合 , 合成 , 复合材料composite insulation 复合绝热层composite Portland cement复合硅酸盐水泥concrete 混凝土concrete batching plant 混凝土搅拌站concrete composition 混凝土配合比concrete block 混凝土砌块condensation polymerization 缩聚反应concrete products 混凝土制品concrete pump 混凝土输送泵condensed silica fume 浓缩 ( 凝聚 ) 的二氧化硅烟雾 ( 硅粉 )conductivity 导热性consistency 稠度corrosion of steel in concrete钢筋的腐蚀cost of concrete 混凝土成本cold bending test 冷弯试验cold-laid bituminous concrete冷铺沥青混凝土coal tar 煤沥青coarse aggregate 粗集料coefficient of variation (Cv) 变异系数cohesion 粘聚cohesiveness 粘聚性cold draw 冷拔cold-laid bituminous mixture冷铺沥青混合料cold stretching 冷拉cold working 冷加工colloid 胶体colloidal structure 胶体结构colloid mill 胶体磨compacting factor 捣实因素composite material 复合材料concrete 混凝土concrete mix 混凝土混合料concrete mix proportion 混凝土配合比continuous grading 连续级配cork 软木cork insulation 软木绝热制品creep 蠕变crack 裂缝cracking 开裂creep 徐变crescent ribbed bars 月牙肋钢筋critical aggregate size 临界集料尺寸critical degree of saturation临界饱和度critical stress 临界应力cross grain 斜纹C-S-H 水化硅酸钙crushing test 压碎试验crushing value 压碎值crystallization 结晶(作用) cryogenic behavior 低温性质curing 养护decay 腐朽dense concrete 密实混凝土defect 缺陷deflection 挠度degree of complex flow 复合流动度degree of hardness 硬度degree of humidity 湿度deicing salts action 除冰盐作用design of concrete mix混凝土配合比设计density 密度dense grading 密级配dicalcium silicate (C2S)硅酸二钙disperse phase 分散相dispersion medium 分散介质drying shrinkage 干燥收缩 ( 干缩 ) ductility 延展性durability 耐久性durability factor 耐久性因素dormant period 垫伏期early-age behavior 早期性质early strength cement 早强水泥early wood 早材asphalt cement 粘稠沥青(膏体沥青) asphalt concrete (地)沥青混凝土alkali-aggregate reaction 碱-集料反应bend stress 弯曲应力binder bonding agent 粘合剂binder 结合料blast-furnace slag 高炉矿渣blast-furnace slag cements 高炉矿渣水泥bleeding 泌水性blending method 调和法blender 搅拌器,打浆机bond 粘结Calcium钙,形成层calcium aluminate 铝酸钙calcium aluminate cement 铝酸钙水泥calcium carbonate 碳酸钙calcium chloride 氯化钙calcium ferroalumnates 铁铝酸钙calcium hydroxide 氢氧化钙calcium lignosulphonate 木质磺酸钙calcium lime 钙质石灰calcium oxide 氧化钙calcium silicate 硅酸钙calcium silicate hydrate(CHS) 水化硅酸钙calcium silicate insulat1on硅酸钙绝热制品calcium sulfates 硫酸钙calcium sulfoaluminate 硫铝酸钙calcium sulfoaluminate hydrates水化硫铝酸钙carbon disulphide 二硫化碳ettringite 钙矾石flint 燧石float test 浮标试验floating 刮平flow of cement mortar 水泥胶砂流动度flow value 流值formwork removal 拆模fine aggregate 细集料final set 终凝fire resistance 耐火性flowing concrete 流动混凝土flexural property 受弯性能flexural rigidity 抗弯刚度 (B)fiber reinforced plastics 纤维增强塑料fiber-glass reinforced plastics 玻璃纤维增强塑料fiber cement 纤维水泥fiber insulation 纤维绝热材料fineness of cement 水泥细度fineness modulus 细度模数(M) finishing 抹面( 修整 )fibre board 纤维板fiber concrete 纤维混凝土fine sand 细砂fiber saturation point 纤维饱和点filler 填料final set 终凝fire point 燃点fly ash 粉煤灰fly-ash cement 粉煤灰水泥flash set 闪凝( 瞬间凝结 )flash point 闪点flexural strength 弯曲强度graph 图表、图解graphical method 图解法gravel 砾石、卵石gradation 级配ground quick lime 磨细生石灰grading / gradation 颗粒级配grading curve 级配曲线grain-size refinement 颗粒尺寸的优化granite 花岗石gel 凝胶gel pores 凝胶孔gel/space ratio 凝胶/空隙比gap-graded aggregate 间断级配集料gas concrete 加气混凝土gap grading 间断级配fraction 组分fracture mechanics 断裂力学fracture toughness 断裂韧性free carbon 游离碳free calcium oxide 游离氧化钙fresh concrete 新拌混凝土freeze-thaw resistance 抗冻融性frost action on aggregate骨料受到冰冻作用frost action on cement paste水泥浆受到冰冻作用frost action on concrete混凝土受到冰冻作用frost resistance 抗冻性gypsum 石膏gypsum concrete 石膏混凝土hardening 硬化hardness 硬度high-early strength cement 早强水泥high-early strength concrete 早强混凝土high performance concrete 高性能混凝土homogeneous materials 均质材料hydrophilic and hydrophobic 亲水与憎水hydrated (Portland) cement paste 已水化的水泥浆hydration of Portland cement 波特兰水泥的水化hydration reaction of aluminates 铝酸盐水化反应hydration reaction of silicates硅酸盐水化反应hydraulic cement 水硬性水泥hydraulic pressure 水压力impact strength 冲击强度igneous rocks for aggregateimpact ductility 冲击韧性impact strength 抗冲击强度impermeability 抗渗性,不渗透性impact resistance 抗冲击性impact test 冲击试验impact toughness 冲击韧度initial set 初凝1ime 石灰lime cement 石灰水泥lime stone 石灰石loss of slump of concrete混凝土的坍落度损失low alloy steel 低合金钢macrostructure 宏观结构magnitude of self-stress 自应力magnesium oxide 氧化镁manganese steel 锰钢manual plastering 手工抹浆map cracking 龟裂marble 大理石masonry cement 砌筑水泥masonry mortar 砌筑砂浆mass concrete 大体积混凝土maximum aggregate size 最大集料粒径maximum crack width 最大裂缝宽度maximum density curve 最大密度曲线maximum size of sand 砂的最大粒径maximum theorical density 理论最大密度mechanical property 力学性质membrane curing 薄膜养护metal 金属metamorphic rock 变质岩mica 云母microcracking 微裂缝microsilica 微细二氧化硅(硅粉)mild steel 低碳钢microstructure 微观结构mineral admixture 矿物外加剂mineral powder 矿粉minimum crack spacing 最小裂缝间距mix design 配合比设计mixing of concrete 混凝土的搅拌mixing water 拌和用水mix proportioning(designing )配合比(设计)mix proportions 配合比mix proportion by absolute volume绝对体积法配合比(设计)mix proportion by loose volume现场松散体积配合比(设计)mix proportion by weight 重量配合比mixed base 混合基mixed-in-place 现场拌和mixed process 混合过程mixing time 拌和时间mixing water 拌和水mixed cement 混合水泥mixture 混合料modility,fluidity流动性modulus of deformation 变形模量(EB) modulus of elasticity 弹性模量modulus of elasticity concrete 混凝土弹性模量moisture 湿度,水分moisture absorption 吸湿率moisture content (MC) 含水量moisture condition 含水状态moisture content of aggregate骨料含水量monosulphalte 单硫酸盐monosulfate hydrate 单硫酸盐水化物mortar theory 胶浆理论mortar consistency 砂浆稠度mortar strength 砂浆强度needle penetrometer 维卡仪penetration index (PI) 针入度指数penetration 针入度Particle size 颗粒尺寸particle size distribution 粒度分布pat test 试饼法penetration resistance 抗贯入性percentage elongation 伸长率percentage passing 通过百分率percentage retained 存留百分率oven-dry aggregate 炉干骨料ordinary Portland cement普通硅酸盐水泥ordinary concrete 普通水泥混凝土open-graded mixture 开级配混合料poisson's ratio 泊松比physical property 物理性质phosphate 磷酸盐placing of concrete 混凝土的浇筑porosity 孔隙率portland cement 波特兰水泥portland blast-furnace slag cement 高炉矿渣波特兰水泥portland pozzolan cement火山灰质波特兰水泥portlandite 氢氧钙石pore-size distribution 孔径分布pozzolan 火山灰pozzolanic reaction 火山灰质反应preplaced aggregate concrete预填集料混凝土pumped concrete 泵送混凝土quality 质量,性质quality control 质量控制quality assurance 质量保证quartz 石英quartz glass 石英玻璃quartz sand 石英砂quartzite 石英岩quick lime 生石灰quick set 快凝quick setting cement 快硬水泥quick-taking cement 快凝水泥quick hardening 水硬性水泥quench 水淬,骤冷rapid setting and hardening cements快凝与快硬水泥raw limestone 石灰石ready-mixed concrete 预拌混凝土recycled-concrete aggregate再生混凝土集料regulated-set cement 调凝水泥reinforced concrete (RC) 钢筋混凝土relative density 相对密度resin 胶质,树脂retarder 缓凝剂retarding admixtures 缓凝外加剂retempering 重新调拌revibration 重新振捣rheological characteristics 流变特性sand 砂sand grading 砂的级配sandstone 砂岩sand grading curve 砂的级配曲线sand grading standard region 砂的级配标准区segregation 离析set retarder admixture 缓凝剂set retarding and water-reducing admixture 缓凝减水剂setting time 凝结时间setting of cement paste 水泥浆的凝结setting of concrete 混凝土的凝结shrinkage 收缩shrinkage-compensating concrete收缩补偿混凝土shrinkage crack 收缩裂缝sieve analysis of aggregate集料的筛分析silica fume 硅粉slag 矿渣slump cone test 坍落度锥体试验slump loss in concrete混凝土中的坍落度损softening point test 软化点试验solid/space ratio 固体/空隙比solid-state hydration 固态水化solidification 凝固作用soundness 安定性specific heat 比热specific surface area 比表面积specifications 规范standard specifications 标准规范stiffening of cement paste 水泥浆的变硬standard deviation 标准差standard error 标准误差standard of concrete 混凝土强度standard sand 标准砂standard sieve 标准筛standard test method 标准试验方法static modulus 静弹性模量strain 应变strength 强度strength at 28days 28天强度strength grade of cement 水泥强度等级strength of cement mortar 水泥胶砂强度strength of cube 立方体强度strength of cylinders 圆柱体强度structure high density concrete高表观密度混凝土结构stress 应力stress concentration 应力集中stressed crack 受力裂缝stress intensity factor 应力强度因素stress-strain curve 应力-应变曲线sulfate attack 硫酸盐侵蚀sulfate resisting cement 抗硫酸盐水泥temperature susceptibility 温度感应性temperature shrinkage 温度收缩temperature effects 温度效应tensile strain 拉伸应变tensile strain capacity 拉伸应变能力tensile strength 拉伸强度(抗拉强度) tetracalcium aluminate hydrate水化铝酸四钙test methods 试验方法test sieve 试验筛testing of material 材料试验testing sieve shaker 试验用振动筛分机test load 试验负荷the particle grading 颗粒级配thermal conductivity 导热性thermal contraction 热收缩thermal diffusivity 热扩散性thermal expansion coefficient热膨胀系数thermal insulation material 绝热材料thermal insulation properties 保温性能timber 木材toughness 韧性trial mixes 试拌混合物tricalcium aluminate 铝酸三钙tricalcium silicate 硅酸三钙uncombined CaO 游离CaOVander Wale force 范德华力vapor pressure 蒸汽压力vacuum insulation 真空绝热vapor barrier / water vapor retarder 隔汽层variegated glass 大理石纹Vebe consistency 维勃稠度void 空隙voids detection 空隙的测定voids ratio 孔隙率void in hydrated cement paste水化水泥浆中的孔隙water 水water absorption 吸水率water / cement ratio 水灰比water content 用水量water content (moisture content)含水率( 湿度 )water-lightness 不透水性water repellent admixture 防水剂water-proof 防水的water proofing admixture 防水剂water proofing compound 防水化合物water-reducing admixtures 减水剂water-reducing retaders 缓凝减水剂water-reducing admixture 普通减水剂workability control 和易性控制workability definition 和易性定义workability 工作性workability of ready-mixed concrete 预拌混凝土和易性workability of light weight concrete 轻混凝土和易性workability measurement 和易性测量。
Materials Science and Engineering A437(2006)436–445Impact toughness and microstructure relationship in niobium-and vanadium-microalloyed steels processed with varied coolingrates to similar yield strengthS.Shanmugam a,R.D.K.Misra a,∗,T.Mannering b,D.Panda b,S.G.Jansto ca Center for Structural and Functional Materials and Department of Chemical Engineering,University of Louisiana at Lafayette,LA70504-4130,USAb Nucor-Yamato Steel,P.O.Box1228,5929East State Highway18,Blytheville,AR72316,USAc Reference Metals,1000Old Pond Road,Bridgeville,PA15017,USAReceived12July2006;accepted3August2006AbstractWe describe here the relationship between microstructure and impact toughness behavior as a function of cooling rate for industrially processed Nb-and V-microalloyed steels of almost similar yield strength(∼60ksi).Both Nb-and V-microalloyed steels exhibited increase in toughness with increase in cooling rates during processing.However,Nb-microalloyed steels were characterized by relatively higher toughness than the V-microalloyed steels under identical processing conditions.The microstructure of Nb-and V-microalloyed steels processed at conventional cooling rate,primarily consisted of polygonal ferrite–pearlite microconstituents,while Nb-microalloyed steels besides polygonal ferrite and pearlite contained significant fraction of degenerated pearlite.The microstructure of Nb-and V-microalloyed steels processed at relatively higher cooling rate contained degenerated pearlite and lath-type(acicular)ferrite in addition to the primary ferrite–pearlite constituents.The fraction of degenerated pearlite was higher in Nb-microalloyed steels than in the V-microalloyed steels.In both Nb-and V-microalloyed steels the precipitation characteristics were similar with precipitation occurring at grain boundaries,dislocations,and in the ferrite matrix.Fine-scale (∼5–10nm)precipitation was observed in the ferrite matrix of both the steels.The selected area diffraction(SAD)pattern analysis revealed that thesefine precipitates were MC type of niobium and vanadium carbides in the respective steels and followed Baker–Nutting orientation relationship with the ferrite matrix.The microstructural studies suggest that the increase in toughness of Nb-microalloyed steels is attributed to higher fraction of degenerated pearlite in the steel.©2006Elsevier B.V.All rights reserved.Keywords:Microalloyed steels;Precipitation;Degenerated pearlite1.IntroductionCurrently,there is a strong interest to study thermomechan-ical processing and accelerated cooling of high strength low alloy steels to derive mechanical property benefits,notably strength–toughness combination[1–8].It is known that cooling rate after the last reduction and coiling temperature has signifi-cant effect on the ultimate microstructure of steels.Accelerated cooling is one of the methods to strengthen the steels with mini-∗Corresponding author at:Center for Structural and Functional Materials and Department of Chemical Engineering,University of Louisiana at Lafayette,P.O. Box44130,Lafayette,LA70504-4130,USA.Tel.:+13374826430;fax:+13374821220.E-mail address:dmisra@(R.D.K.Misra).mal alloying content and to obtain good toughness.It also facil-itates the development of high strength steels with low carbon and manganese content,and consequently improved weldability [2].The lowering of ferrite transformation temperature intro-duced by higher cooling rate promotes ferrite nucleation rate at the austenite grain boundaries and in the grain interior.The enhanced nucleation density restricts grain growth because of impingement of mutual grains,resulting in ferrite grain refine-ment[2].Additionally,the volume fraction of non-equilibrium phases increases with higher cooling rates[1–6].Thus,accel-erated cooling after controlled rolling produces afine-grained microstructure and promotes the formation of low transforma-tion temperature products,such as degenerated pearlite,bainitic ferrite,acicular ferrite or bainite and martensite–austenite constituent in microalloyed steels[1,2,5,6].In general,theS.Shanmugam et al./Materials Science and Engineering A437(2006)436–445437strength of C–Mn steels is enhanced because of replacement of pearlite phase by lath-like bainite using high cooling rate[1].Majority of the bainitic microstructures obtained in low carbon-microalloyed steels are described as bainitic ferrite or acicular ferrite and granular bainite.Sometimes a mixed microstructure is also obtained in HSLA low carbon steels at high cooling rate[1–8].As the cooling rate increases,the phase transformation temperature,Ar3,decreases and transfor-mation occurs at a rate such that it passes through the two-phase region quickly and dynamic precipitation of ferrite is mini-mum[3].Also,the deformation enhances the transformation driving force and accelerates the continuous cooling transfor-mation,shifting the pearlite transformation curve of CCT dia-gram to the right.When the cooling rate is increased to the extent that the ferrite transformation temperature is surpassed,a fully bainitic microstructure is obtained[8].Accelerated cooling refines bainitic microstructure and is attributed to the increase in the driving force for the nucleation rate of ferrite subunits as a consequence of reduction in the bainite transformation start temperature[6,7].A decrease in the bainite transformation start temperature increases the difference in the free energy between austenite and bainite that favoring the formation of bainite.The growth offine bainitic ferrite laths is controlled by nucleation rate of subunits,which in turn strongly depends on the driving force(undercooling)for the phase transformation reaction[6,7].Considering that currently,there is increased demand for high strength structural beams with superior toughness,we are pur-suing microalloying approach to process structural beams with high strength–toughness combination.The present paper is an effort in this direction,where the focus is to study the effect of cooling rate on the mechanical behavior and relate to microstruc-tural features.2.Steel composition and experimental methodsThe chemical composition range of Nb-and V-microalloyed steels is presented in Table1.The composition range meets the ASTM specification A992.The niobium content required to obtain the desired yield strength of55–60ksi was approx-imately one third of the vanadium content.The processing conditions were similar for both Nb-and V-microalloyed steels with no intentional differences.The processing parameters are not described here due to proprietary reasons.A representative beam size is W24×103;the designated size means that the nominal depth of beam is24in.,when the beam is lying in the Table1Chemical composition range of Nb-and V-microalloyed steelsElements Nb-microalloyed steel(wt.%)V-microalloyed steel(wt.%) C0.030–0.1000.030–0.100Mn0.500–1.5000.500–1.500V0.0010.020–0.050Nb0.020–0.0500.001Si0.15–0.250.15–0.25P0.010–0.0200.010–0.020h-position with the web horizontal,the width is close to24in. The103refers to nominal weight in lbs/ft.Mean grain size was determined by the linear intercept method.Intercept lengths were determined and then converted to nominal grain size using standard tables.Tensile tests were done according to ASTM E8and ASTM A370specifications and Charpy v-notch impact test was carried out according to ASTM E23and ASTM A673standards.Small coupons were cut from the beams and mounted for metallographic examination.Standard grinding and polishing techniques were employed,and specimens were etched with 2%nital.Light microscopy and scanning electron microscopy (JEOL6300F)imaging techniques were used to obtain low mag-nification images that revealed the overall microstructure.The amount of different microstructural constituents was estimated with conventional point-counting techniques in association with a square point grid as described below.The metallographic mea-surements were made on at least20fields-of-view in order to obtain representative data for stereological analysis.Stereological analysis was adopted as one of the approach to understand the underlying differences in toughness of steels, since our recent work indicated that small differences in tough-ness of steels with similar yield strength can be explained in terms of stereological parameters,notably,contiguity ratio[9]. The parameters determined for stereological analysis were vol-ume fraction,mean intercept length,and contiguity ratio.The volume fraction of ferrite V V␣was calculated using the systematic point count method.Ferrite grain size and pearlite colony size was estimated in terms of mean intercept length (¯L␣)determined by the following expression[9]:¯L␣=V V␣×L TN␣(1)where V V␣is the volume fraction of ferrite phase,N␣the number of ferrite grains intercepted by the test lines and L T is the line length of the test lines.The ferrite contiguity ratio C␣was calculated by Eq.(2)[9]:C␣=2(S V)␣–␣(S V)␣–P+2(S V)␣–␣=2(P L)␣–␣(P L)␣–P+2(P L)␣–␣(2)where(P L)␣–␣is the number of point intersections per unit length of the test line with ferrite–ferrite,(P L)␣–P the num-ber of point intersections per unit length of the test line with ferrite–pearlite boundaries,(S V)␣–␣the surface area per unit vol-ume of ferrite–ferrite boundaries and(S V)␣–P is the surface area per unit volume of ferrite–pearlite boundaries.Contiguity is defined as the fraction of the total interface area of phase that is shared by grains of the same phase.Thus, ferrite contiguity ratio is indicative of the amount of ferrite that is continuous,i.e.,it tells how much ferrite is adjacent to the ferrite. It is calculated byfinding the ratio of number of ferrite–ferrite grain boundaries to the total number of grain boundaries in the microstructure(Eq.(2)).From Eq.(2),contiguity ratio will vary from0to1.Transmission electron microscopy was carried out on thin438S.Shanmugam et al./Materials Science and Engineering A 437(2006)436–445to ∼100m in thickness.Three-millimeter discs were punched from the wafers and electropolished using a solution of 10%perchloric acid in acetic acid electrolyte.Foils were examined with a JEOL FEG TEM/STEM operated at 200kV .3.Results and discussion 3.1.Tensile and impact behaviorTensile properties of Nb-and V-microalloyed steels are listed in Table 2for conventionally/normally cooled beams.Both the steels exhibited similar yield strength,tensile strength,and per-cent elongation.Almost similar values were obtained at inter-mediate and high cooling rates.However,there was variation in toughness of the two steels as schematically depicted in Fig.1.Table 2Representative room temperature tensile properties of Nb-and V-microalloyed steels PropertiesNb-microalloyed steel V-microalloyed steel Yield strength (ksi)57–6058–61Tensile strength (ksi)72–7475–76%Elongation23–2623–25Fig.1shows the variation in impact toughness of Nb-and V-microalloyed steels as a function of cooling rate.It may be noted that both the steels generally experienced improvement in toughness with increase in cooling rate.However,the toughness improvement appeared to be greater for the Nb-microalloyed steel as compared to the V-microalloyed steel.3.2.Microstructures of Nb-and V-microalloyed steels Representative scanning electron micrographs of Nb-and V-microalloyed steels are presented in Figs.2and 3.The low-and high-magnification micrographs of Nb-microalloyed steels processed at conventional (low)and high cooling rates are presented in Fig.2a,b and c,d,respectively.Similarly,the micrographs of V-microalloyed steels processed at conventional and high cooling rates are presented in Fig.3a,b and c,d,respectively.The primary microstructural constituents of Nb-and V-microalloyed steels processed at conventional and high cooling rates were polygonal ferrite,pearlite,and degenerated pearlite.It may,however,be noted that the fraction of degen-erated pearlite was high for the steels subjected to relatively high cooling rate (Fig.1b and Table 3),and at a given cooling rate,the Nb-microalloyed steel contained significantly higher amount of degenerated pearlite (Fig.2c and d)as compared to the V-microalloyed steels (Fig.3c and d).The average fer-rite grain size of both the steels processed at conventional and high cooling rates was similar (∼26–29m).The quantitative metallographic data for Nb-and V-microalloyed steels are sum-marized in Table 3.The microstructures of Nb-and V-microalloyed steels pro-cessed at conventional (normal)cooling rate are presented in Figs.4and 5.The general microstructure and the dislocation substructure in ferrite of Nb-microalloyed steels are presented in Fig.4a and b,respectively.The representative low magnification TEM micrographs show large polygonal ferrite grains with high dislocation density.There were some grains that were virtually free of dislocations.Fig.5a and b shows the general microstruc-ture and dislocation density in ferrite of V-microalloyed steels.Representative bright field TEM micrographs of Nb-and V-microalloyed steels subjected to relatively high cooling rate are presented in Figs.6and 7.Two types of ferrite morpholo-gies (polygonal ferrite and lath-type ferrite)were observed in both the steels.The microstructure of Nb-microalloyed steels showing regions of polygonal ferrite,lath-type ferrite grains and degenerated pearlite are presented in Fig.6.Similarly,the microstructures of V-microalloyed steels that contain polygonal ferrite,lath-type ferrite grain structure and degenerated pearlite are presented in Fig.7.At higher cooling rates,it is anticipated that austenite transforms to fine ferrite crystals in the interme-diate temperature range as compared to the conventional ferrite structure.In Figs.6and 7,the ferrite grains in groups of parallel laths are termed as acicular ferrite or bainitic ferrite [10].3.2.1.Degenerate pearliteDegenerated pearlite is formed by nucleation of cementiteS.Shanmugam et al./Materials Science and Engineering A437(2006)436–445439Fig.2.Representative low-and high-magnification scanning electron micrographs of Nb-microalloyed steel processed at(a and b)conventional and(c and d)high cooling rates.The micrographs(b)and(d)show degenerated pearlite.temperature between normal pearlite and upper bainite[11].A schematic diagram illustrating the formation mechanism of degenerated pearlite is presented in Fig.8.Since the advanc-ing ferrite/austenite is enriched with carbon by partitioning process,it is believed that cementite nucleation takes place at ferrite/austenite interface boundary.Similar to lamellar pearlite, degenerated pearlite is also formed by diffusion process and con-sidering its morphology,the difference is attributed to the insuf-ficient carbon diffusion to develop continuous lamellae[12]. It is reported that the interface between ferrite and cementite in degenerated pearlite is wider than the conventional pearlite, thus the ferrite grain boundary area of the controlled-rolled steels that contains degenerated pearlite is higher as compared to the conventionally processed steel[13].A typical brightfield TEM micrograph of degenerated pearlite formed in Nb-microalloyed steel is presented in Fig.9a and the correspondingselected440S.Shanmugam et al./Materials Science and Engineering A437(2006)436–445Table3Microstructural features of Nb-and V-microalloyed steelsProperties Nb-microalloyed steels V-microalloyed steelsConventional cooling rate Higher cooling rate Conventional cooling rate Higher cooling rate FerriteArea fraction(%)82.4±3.182.8±0.0283±2.582.8±3.8 Mean intercept length(¯L␣)(m)27±1.527±2.828.9±325.9±1 Contiguity ratio(C␣)0.740.760.770.74PearliteArea fraction(%)9.6±3.1 1.2±1.917±2.38.2±2.9 Mean intercept length(¯L␣)(m)10.3±0.710.2±0.78.4±0.98.9±1 Degenerated pearliteArea fraction(%)8±0.916±2–9±1Fig.4.Brightfield TEM micrographs of Nb-microalloyed steels processed at conventional(or normal)cooling rate showing(a)polygonal ferrite structure and(b) dislocation substructure in ferrite.area diffraction(SAD)pattern is shown in Fig.9b.The SADpattern analysis suggested that the cementite platelets exhibit[112]␣//[122]Fe3C orientation relationship with ferrite matrix,which is close to‘Pitsch’orientation relationship that is com-monly observed in lamellar pearlite.Degenerated pearlite is a microstructural constituent believed to promote toughness in steel[13].3.3.Precipitation in Nb-and V-microalloyed steelsFig.10a and b shows grain boundary precipitation and pre-cipitation on dislocations in ferrite region of Nb-microalloyed steels,while Fig.11a shows precipitation in ferrite matrix together with the corresponding selected area diffraction(SAD) pattern in Fig.11b.The SAD pattern analysis indicatedthatS.Shanmugam et al./Materials Science and Engineering A437(2006)436–445441Fig.6.Brightfield transmission electron micrographs of Nb-microalloyed steels processed at relatively high cooling rate showing(a)polygonal ferrite structure(b) lath-type(acicular)ferrite structure and(c)degenerated pearlite.Fig.7.Brightfield transmission electron micrographs of V-microalloyed steels processed at relatively high cooling rate showing(a)polygonal ferrite structure,(b) lath-type(acicular)ferrite structure and(c)degenerated pearlite.Fig.8.Schematic diagram illustrating the formation mechanism of degenerated pearlite.Table4Precipitate characteristics of Nb-and V-microalloyed steelsProperties Nb-microalloyed steels V-microalloyed steelsConventional cooling rate Higher cooling rate Conventional cooling rate Higher cooling rate Mean particle size(d)(nm) 5.25±3.57.5±4.510.3±48±4.3442S.Shanmugam et al./Materials Science and Engineering A437(2006)436–445Fig.9.Brightfield TEM micrographs of Nb-microalloyed steels showing(a)degenerated pearlite and(b)SAD pattern analysis for degenerated pearlite shown in (a).Fig.10.Brightfield TEM micrographs of Nb-microalloyed steels showing(a)grain boundary precipitation and(b)precipitation on dislocations.S.Shanmugam et al./Materials Science and Engineering A437(2006)436–445443Fig.12.Brightfield TEM micrographs of V-microalloyed steels showing(a)grain boundary precipitation and(b)precipitation on dislocations.thefine precipitates were MC type of cubic niobium carbides and the precipitates exhibited[100]␣//[110]NbC Baker–Nutting orientation relationship with the ferrite matrix.Grain boundary precipitation and precipitation on dislocations in ferrite region of V-microalloyed steels was also observed and is presented in Fig.12.Fig.13a shows precipitation in ferrite matrix of V-microalloyed steels and the corresponding selected area diffrac-tion(SAD)pattern is shown in Fig.13b.In a manner similar to Nb-microalloyed steel the SAD pattern analysis indicated that thefine precipitates were MC type of cubic vanadium carbides and the precipitates exhibited a cube–cube[001]␣//[001]VC Baker–Nutting orientation relationship with the ferrite matrix. The characteristics of precipitates in terms of mean particle size,mean inter-particle distance and particle density in ferrite matrix of both Nb-and V-microalloyed steels are summarized in Table4.The above results suggest that Nb-and V-microalloyed steels experienced strain induced precipitation at grain boundaries,and dislocations,while thefine precipitates in ferrite formed during cooling.The precipitation of microalloying elements occurs dur-ing various stages of thermomechanical processing of steels.At soaking temperatures,the microalloying elements,Nb and V,are taken into solution depending on the limitation imposed by the solubility product.For carbide and nitride forming elements,the solubility in austenite at any given temperature depends on C and N content of the steel.When the temperature is lowered during cooling,supersaturation of these solute elements increases and precipitation begins at favorable kinetic conditions.Deforma-tion of austenite introduces large amount of lattice defects such as dislocations and vacancies that assist the diffusional process that control the precipitation kinetics.As a result,strain induced precipitation occurs at the prior austenite grain boundaries or defects.In summary,the Nb-and V-microalloyed steels exhib-ited similar precipitation behavior in ferrite and the size range was from∼5to10nm(Table4).It is reported that the effec-tive size range for precipitation hardening is∼5–20nm[9,14]. Thesefine precipitates exhibited Baker–Nutting orientation rela-tionship(Figs.11b and13b)with the ferrite matrix of Nb-and444S.Shanmugam et al./Materials Science and Engineering A 437(2006)436–445Fig.14.Schematic illustration of deformation of cementite in lamellar pearlite and degenerated pearlite.V-microalloyed steels,confirming that the precipitation occurred in ferrite.3.4.Toughness behavior of Nb-and V-microalloyed steelsIn the present case the microstructural parameters that are likely to influence toughness are ferrite grain size,degenerated pearlite,and acicular ferrite.A finer grain size and higher conti-guity ratio is expected to impart higher toughness.From Table 3,it may be noted that the ferrite grain size and ferrite contiguity ratio are similar for both the steels processed at conventional and relatively high cooling rates.However,there are significant differences in the area fraction of degenerated pearlite for the two steels (Fig.1b and Table 3).A schematic diagram illus-trating the nature of cementite plates present in the lamellar pearlite and degenerated pearlite and its effect on plastic defor-mation is presented in Fig.14a and b.It is reported that the cementite thickness in degenerated pearlite is finer as compared to the conventional pearlite (Fig.14b),and hence the volume fraction of cementite and ferrite are different in the former as compared to the latter [15].Coarse pearlite deforms inhomo-geneously (Fig.14a)with strain localized in narrow slip bands,where as fine degenerated pearlite is expected to experience uni-form strain distribution during deformation.It is also shown that the steels containing degenerated pearlite with specific cementite thickness exhibit maximum ductility [15].It is also reported that though cementite is characterized by hard and brittle in nature,it can endure large strain when the cementite platelets are thinner [16].Thus,at present,we believe that the increase in the tough-ness of Nb-and V-microalloyed steels at relatively high cooling rate is a consequence of higher fraction of degenerated pearlite and the presence of lath-type ferrite.While,the higher toughness of Nb-microalloyed steels in relation to V-microalloyed steels at conventional or normal cooling rate is a consequence of higher fraction of degenerated pearlite,with ferrite grain size being similar for the two steels.The above data is further supported by the recent observations nantly bainitic ferrite with increase in cooling rate is responsi-ble for the strength–toughness combination of Nb-microalloyed steels at high cooling rate.4.Conclusions1.At conventional cooling rates employed in the mill,the microstructure of Nb-and V-microalloyed steels primarily contained polygonal ferrite–pearlite,while Nb-microalloyed steels contained significant fraction of degenerated pearlite.The Nb-and V-microalloyed steels processed at relatively higher cooling rate compared to conventional or normal cooling rate contained degenerated pearlite and lath-type (acicular)ferrite in addition to the primary ferrite–pearlite constituents.The fraction of degenerated pearlite was higher in Nb-microalloyed steels than in the V-microalloyed steels.2.Both Nb-and V-microalloyed steels exhibited similar precip-itation characteristics with precipitation at grain boundaries,dislocations and in the ferrite matrix.Fine-scale (∼5–10nm)precipitation occurred in the ferrite matrix of both the steels.The SAD pattern analysis revealed that these fine precipitates were MC type niobium and vanadium carbides in the respec-tive steels and obeyed Baker–Nutting orientation relationship with the ferrite matrix.3.The Nb-and V-microalloyed steels experienced improve-ment in toughness with increase in cooling rates during processing.However,Nb-microalloyed steels seem to exhibit relatively higher toughness than the V-microalloyed steels during processing at conventional and high cooling rates.The increase in toughness of Nb-microalloyed steels is 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