轻质钢的研究进展(一)——富Al无间隙原子钢和铁素体轻质钢

轻质钢是在超低碳钢或C-Mn钢基础上添加Al元素而形成的Fe-Al或Fe-Mn-Al-C合金钢。简要介绍了Al元素对钢的密度、相组织构成和基体碳化物形成的影响,并依据合金成分和相组织构成将轻质钢大致分为单一铁素体钢(多为富Al无间隙原子钢,即Al-IF钢)、铁素体钢(多为δ-TRIP钢)、铁素体—奥氏体双相钢和奥氏体钢四类。重点阐述了Al-IF钢和δ-TRIP钢的微观组织特征、力学性能和强韧化机制,为进一步研究开发上述种类轻质钢提供参考。     

Fe-Mn-Al-C系轻质高强钢研究现状及展望

 Fe-Mn-Al-C轻质钢以低密度、高强塑性等优势,高度契合汽车等行业减重、加工和安全性等需求期望,具有巨大应用潜力。然而,当前关于轻质钢制备、加工、服役等相关研究结论不尽一致,制约着轻质钢的开发、应用。因此,以Fe-Mn-Al-C系轻质高强钢中的奥氏体作用机制为着眼点,首先对比了不同学者对轻质钢成分和热机械作用对奥氏体热稳定性的影响研究;其次,结合作者对奥氏体TWIP钢的相关研究,分析了奥氏体协调位错运动特征以及协调变形机制及与强韧化关联机理;然后,依据奥氏体的作用机制,对轻质钢在不同载荷下的力学性能响应也进行了分析。最后,对现有的研究进行了总结,提出了Fe-Mn-Al-C系轻质高强钢的研究展望,旨在为更多的研究提供参考。     

锰铬奥氏体钢的加工硬化及耐磨性的研究

本文研究了锰铬奥氏体钢的加工硬化能力及耐磨性。实验证明,较低的碳含量(C1.10～1.20％)及铬的加入(Cr2.0～2.5％)使奥氏体层错能降低,在形变时形成大量形变孪晶,孪晶带薄,孪晶间距小并且有ε马氏体出现。这是钢的强化和加工硬化能力提高的主要原因。在冲击载荷作用下,锰铬奥氏体钢的加工硬化速度快,可以迅速形成高硬度的稳定的硬化层,抗冲击磨料磨损的能力大幅度提高。模拟磨损试验和工业验证都表明,锰铬奥氏体钢较传统的Mnl3的加工硬化能力和耐磨性有明显提高,在冲击磨料磨损条件下可取代Mn13,有广阔的工业应用前景。     

奥氏体化时间对DP780冷轧双相钢组织和性能的影响

用连续退火模拟机研究了850℃奥氏体化时间(30～100 s)对1 mm厚DP780冷轧双相钢板(%:0.15C、1.80Mn、0.08Ti、0.04Al)组织和力学性能的影响。结果表明,当奥氏体化温度为850℃,以24℃/s冷却至460℃停留12 s,再以7℃/s冷却至室温的情况下,通过改变奥氏体化时间,可改变钢中马氏体含量和钢的抗拉强度。当奥氏体化时间较短时,马氏体呈带状连续分布,当奥氏体化时间较长时,马氏体带状连续性减弱;当奥氏体化时间在30、45、100 s时,该双相钢马氏体含量分别为13.7%、21.6%和15.6%,抗拉强度分别为800、840、805MPa。     

加热温度对钛微合金化钢奥氏体晶粒长大的影响

通过将钛微合金化钢在箱式电炉中加热至850~1 250℃保温30 min,观察其奥氏体晶粒组织及Ti的析出粒子分布情况,研究钛微合金化钢奥氏体晶粒长大行为及Ti的固溶规律。结果表明:随着加热温度的升高,试验钢存在两个奥氏体晶粒粗化温度,分别为1 050℃和1 250℃,与Ti两种析出粒子的固溶温度相对应,但数值比固溶温度低。分析奥氏体晶粒两个阶段的长大过程发现,随着TiC析出粒子的溶解,晶粒长大激活能从265.6 k J/mol降低至239.8 k J/mol。     

锰对贝氏体钢中残余奥氏体回火稳定性的影响

为探索锰含量的变化(锰质量分数为0.1%(0.1Mn钢)和1.5%(1.5Mn钢))对无碳化物贝氏体钢中残余奥氏体(RA)回火稳定性的影响,利用扫描电镜(SEM)、电子背散射衍射(EBSD)及透射电镜(TEM)等试验方法对残余奥氏体稳定性和力学性能的变化规律进行研究。结果表明,0.1Mn钢的热轧态组织主要是由粒状贝氏体(GB)+板条贝氏体(LB)组成,而1.5Mn钢的热轧态组织主要以板条贝氏体为主,且1.5Mn钢中残余奥氏体含量较高,屈服强度和抗拉强度均优于0.1Mn钢。在经过300～500℃回火后,残余奥氏体体积分数逐渐下降至完全分解,屈服强度和抗拉强度均表现为先升高后降低,但伸长率逐步增加。300℃回火性能最佳,原因主要是由于残余奥氏体在300℃回火中,块状残余奥氏体分解为过饱和马氏体/贝氏体,碳从过饱和马氏体/贝氏体中扩散至邻近残余奥氏体中使其含量增加,热稳定性得到提高,在拉伸的过程中产生了TRIP效应,从而使试验钢的强塑性得到提升。1.5Mn钢的性能明显优于0.1Mn钢,因为锰可以与碳产生协同作用共同促进奥氏体的稳定,提高伸长率,另外锰含量的增加使碳当量也提高,强度增强。基于修...     

Fe-Mn-Al-C系奥氏体基低密度钢的研究进展

 轻量化且高强韧化已成为汽车用钢的主要发展方向。在不同类型的轻质钢中,Fe-Mn-Al-C系奥氏体基低密度钢因具有更高的比强度和良好的塑韧性备受研究者们青睐。从成分体系与力学性能、多种强韧化机制、不同变形机制及工艺调控等方面总结了Fe-Mn-Al-C系奥氏体基低密度钢的研究进展,重点阐述了奥氏体基低密度钢中特有的B2相以及κ-碳化物、MC碳化物等析出相的析出行为对强韧性机制的影响。最后,结合目前国内外学者对Fe-Mn-Al-C系奥氏体基低密度钢的最新研究成果,对奥氏体基低密度钢进行了展望。     

热轧低氮18CrMnB钢奥氏体晶粒粗化行为

本文研究了热轧工艺及含Ti量对低N的18CrMnB钢奥氏体晶粒长大倾向的影响。结果表明,热轧压下率及终轧温度对18CrMnB钢奥氏体晶粒长大倾向的影响不太显著,且不呈简单的变化规律,含Ti量对奥氏体晶粒长大倾向影响很大,当含Ti量超过0.053%时,奥氏体晶粒长大倾向明显减少。     

微合金元素B对轻质TWIP钢组织及力学性能的影响

摘要：将质量分数为0.002%的微合金元素B加入至Fe-28Mn-9Al轻质TWIP钢中，以期改善其强塑积及室温冲击性能。利用X射线衍射、扫描电镜、电子万能拉伸试验机和金属摆锤冲击试验机对热轧TWIP钢的物相组成、微观组织、力学拉伸性能及室温冲击韧性进行了研究与分析。结果表明，微合金元素B的添加具有延缓奥氏体向铁素体转变的作用，细化了奥氏体晶粒，提升了钢的力学性能，TWIP钢的塑性、强塑积和冲击韧性均有明显的提高。     

预备热处理对508-3钢奥氏体晶粒尺寸的影响

试验用钢508-3(/%:0.19C、0.26Si、1.48Mn、0.009F、0.007S、0.78Ni、0.50Mo、0.003Al)由真空感应炉冶炼,50kg铸锭,经1150℃锻成Φ16 mm棒材,终锻≥900℃。研究了正火温度(900～1 200℃)和多次正火工艺(900～1 200℃1 h-900℃1 h-890℃1 h)对508-3钢奥氏体晶粒尺寸的影响。结果表明,在900～1 200℃正火时,随着正火温度升高,奥氏体晶粒尺寸出现明显粗化,奥氏体晶粒度级别由6.5级粗化到3级。随后经过900℃二次正火,钢中原粗大的奥氏体晶粒可以细化到6级,再进行890℃三次正火后,奥氏体晶粒细化不明显。多次阶梯正火处理可以细化508-3钢粗大的奥氏体晶粒,但在同一温度重复正火时,钢中晶粒细化效果不明显。     

Experimental and DFT study on cerium inclusions in clean steels

To provide insights into deforming Ce-O-S-Al inclusions in steels and improving the mechanical properties,the evolution process of such harmful inclusions in clean steels was investigated by thermodynamic calculation,metallographic examination and first-principles calculation in this paper.For the tested IF steel,the thermodynamic analysis results are consistent with the calculated formation enthalpy.After Ce addition,the inclusions are transformed from Al₂O₃and TiN-Al₂TiO₅-Al₂O₃to Ce2O₃,Ce₂O₂S,CeAlO₃,TiN-Al₂TiO₅-Ce₂O₃and TiN-Al₂TiO₅-Ce₂O₂S composite inclusions,which can be confirmed by metallographic examination.The elastic constants were calculated,and the bulk modulus,Young's modulus,shear modulus and Poisson's ratio were evaluated by the Voigt-Reuss-Hill(VRH)approximation.All inclusions except Ce₂O₃show apparent brittleness.TiN,Al₂O₃,Al₂TiO₅and CeAlO₃present much higher hardness than iron matrix,while the hardness of Ce2O₃or Ce₂O₂S is close to that of iron matrix.The thermal expansion coefficients of Ce₂O₃and CeAlO₃are close to that of iron matrix,whereas,Ce₂O₂S inclusion has largely different thermal expansion coefficient from iron matrix and may deteriorate the steel performance at higher temperatures.The relatively small differences between Ce inclusions and iron matrix in terms of hardness,toughness,brittleness,and thermal expansion coefficient can explain the improvement of the mechanical properties of the tested steel.     

Decarburization kinetics of low alloy ferritic steels in sodium

The rates of decarburization of low alloy and plain carbon steels in static, isothermal sodium have been measured over the temperature range 1000° to 1300°F. Low alloy steels studies in these tests were 2-1/4 Cr-1 Mo (T22), 2-1/4 Cr-1Mo-1Nb,and 2-1/4 Cr-1Mo-low carbon (0.015 C). Plain carbon steels studied were 1020, 1040, and 1095. Periodic measurements of the specific carbon loss (mass of carbon lost per unit surface area of specimen) revealed that the decarburization of normal 2-1/4 Cr-1 Mo steel is controlled by diffusivity and solubility of carbon in the matrix. Decarburization rate constants measured in this study for the normal 2-1/4 Cr-1 Mo steel were found to be in good agreement with rate constants calculated from data reported in previous studies. Tests of modified 2-1/4 Cr-1 Mo steels showed that: a) the carbon content of the niobium-stabilized steelwill either remain unchanged or will increase and b) the low carbon steel will decarburize slightly during exposures in the same sodium systems which produce rapid decarburization of the steel with normal amounts of carbon. Decarburization tests on plain carbon steels revealed that both the depths of the decarburized layer and the specific carbon losses were controlled by diffusivity and solubility in the matrix. Comparison of the measured decarburization rate constants with theoreticalvalues (based on a moving-boundary diffusion process) were in good agreement. These data were used to calculate the carbon content at the surfaces of the steels during decarburization in the liquid and vapor phases of a sodium system. It was demonstrated that plain carbon steels can serve as carbon monitors for sodium systems.     

Elastic limit and microplastic response of hardened steels

Tempered martensite-retained austenite microstructures were produced by direct quenching a series of 41XX medium carbon steels, direct quenching and reheating a series of five 0.8C-Cr- Ni-Mo steels and intercritically austenitizing at various temperatures, and quenching a SAE 52100 steel. All specimens were tempered either at 150 °C or at 200 °C. Specimens were subjected to compression and tension testing in the microstrain regime to determine the elastic limits and microplastic response of the microstructures. The retained austenite and matrix carbon content of the intercritically austenized specimens were measured by X-ray diffraction and Mossbauer spectroscopy. The elastic limit of the microstructures decreases with increasing amounts of retained austenite. Refining of the austenite distribution increases the elastic limit. Low elastic limits are mainly due to low flow stresses in the austenite and not internal stresses. The elastic limit correlates with the largest austenite free-mean path by a Hall-Petch type equation. The elastic limit increases with decreasing intercritical austenitizing temperature in the SAE 52100 due to (1) a lower carbon content in the matrix reducing the retained austenite levels and (2) retained carbides that refine grain size and, therefore, the austenite distribution in quenched specimens. The microplastic response of stable austenite-martensite composites may be modeled by a rule of mixtures. In the microplastic region, the strain is accommodated by successively smaller austenite regions until the flow strength matches that of the martensite. Reheating and quenching refines the microstructure and renders the austenite unstable in the microplastic regime, causing transformation of the austenite to martensite by a strain-induced mechanism. The transformation of austenite to martensite occurs by a stress-assisted mechanism in medium carbon steels. The low elastic limits in medium carbon steels were due to the inability of the strain from the stress-assisted transformation of austenite to martensite to balance the plastic strain accumulated in the austenite.     

Cold-rolling technologies of advanced high strength steels in Ansteel

Low - carbon becomes a high - frequency and fashionable word which gets the greatest concern in the world.Low - carbon refers to a minimal output of greenhouse gas emissions into the biosphere, specifically refers to the greenhouse gas carbon dioxide.To reduce energy consumption of automobile,more and more high strength steels are used by vehicle companies.To meet the request of vehicle companies, various high strength steels are developed in steel companies all over the world.Ansteel can provide,ultra-low carbon bake hardening(BH) steels,dual phase(DP) steels and transformation - induced plasticity (TRIP) steels with the grades of under 780 MPa,up to now.AHSS steels have much different composition, microstructure and strenght than conventional vehicle steels,so there are some trouble in producing in cold rolling mills,for example,difficult to join,poor thickness and flatness,accurate temperature and velocity control and so on.To reduce the opportunity of strip breakage,we have done many welding experiments and special research.Now,DP and TRIP steels can be continuously produced in Ansteel.To assure thickness and flatness of strips,we optimized the hot rolling parameter to get low deformation resistance,optimized rolling oil to get fit frictional coefficient and fix on the targat rolling curve.To get more accurate and repetitive results over the production shifts,the Mathematical Model(MM) is used in Ansteel.The MM analyses information transmitted by various sensors and transmitters,compares the collected data with the chosen parameters and adjusts the settings of the various pieces of equipment to hone on the parameter setpoints.At present,the key production technologies of AHSS were grasped by cold rolling mill Ansteel,and Ansteel is the first company to apply the TRIP with the grade of 780 MPa.     

Microstructures and mechanical properties of ferrite-based lightweight steel with different compositions

The microstructures and mechanical properties of ferrite-based lightweight steel with different compositions were investigated by tensile test,scanning electron microscopy(SEM),transmission electron microscopy(TEM),X-ray diffraction(XRD)and thermodynamic calculation(TC).It was shown that the ferrite-based lightweight steels with 5wt.%or 8wt.%Al were basically composed of ferrite,austenite andκ-carbide.As the annealing temperature increased,the content of the austenite in the steel gradually increased,while theκ-carbide gradually decomposed and finally disappeared.The mechanical properties of the steel with 5wt.%Al and 2wt.%Cr,composed of ferrite and Cr7C3carbide at different annealing temperatures,were significantly inferior to those of others.The steel containing 5wt.%Al,annealed at 820°C for 50sthen rapidly cooled to 400°C and held for 180s,can obtain the best product of strength and elongation(PSE)of 31242MPa·%.The austenite stability of the steel is better,and its PSE is higher.In addition,the steel with higher PSE has a more stable instantaneous strain hardening exponent(n value),which is mainly caused by the effect of transformation induced plasticity(TRIP).When theκ-carbide or Cr7C3carbide existed in the microstructure of the steel,there was an obvious yield plateau in the tensile curve,while its PSE decreased significantly.     

Evaluation of the elastic modulus of steels

Literature data on the physical properties of steels have been collected and put into a database. The elastic modulus of steels has been analyzed as a function of composition. An overview over former studies is given. The steels have been investigated in three groups, martensitic and ferritic steels, ferritic steels separately, and austenitic steels. For the last two groups, a thermodynamic analysis with Thermo‐Calc has been performed. Regression analysis on the influence of composition on the elastic modulus was then carried out. The results for ferritic steels reveal that cementite has no effect on the elastic modulus, whereas Cr, Mo, Si, Mn, and Cu increase it. The elastic modulus of austenitic steels is reduced by Ni and Mo and increased by N, NbC, TiC, and Cr. Cr₂₃C₆, while statistically significant in the analysis, has no effect on the elastic modulus of austenitic steels. The regression coefficients found can be used to predict the elastic modulus of steels with known composition.     

Effect of hot‐rolling conditions on the tensile properties of multiphase steels exhibiting a TRIP effect

TRIP‐assisted multiphase steels have been thoroughly studied in the cold‐rolled and annealed state. The effects of hot‐rolling conditions on these steels are much less studied even though these are of major importance for industrial practice. This study was carried out in order to understand the effect of the hot deformation of austenite on the tensile properties of TRIP‐assisted multiphase steels. Two different compositions and microstructures are investigated. The first one is a low‐carbon steel (mass content of 0.15 %) with a microstructure consisting of an intercritical ferritic matrix, bainite and retained austenite. The second one is a medium‐carbon steel (mass content of 0.4 %) that consists of bainite and retained austenite. Both steels were deformed to various strain levels below the non‐recrystallisation temperature of austenite. The medium carbon steel was deformed in the fully austenitic temperature range whereas the low‐carbon steel was deformed in the intercritical temperature range. In both cases, the prior hot deformation of austenite brings about a large enhancement of the work‐hardening capabilities. In the case of the medium‐carbon steel, this effect can be attributed to a much larger TRIP effect taking place during straining. In the case of the low‐carbon steel, the improvement of the work‐hardening behaviour was attributed to an Interaction between the martensitic transformation and the dislocations already present within the surrounding ferrite matrix.     

Fe-12Mn-7Al-0.6C-(V)轻质钢力学行为

为减轻汽车用钢的质量，实现汽车轻量化设计，研究了冷轧Fe 12Mn 7Al 0.6C (V)轻质钢在不同温度下退火的组织和力学行为。结果表明，随着退火温度的升高，奥氏体体积分数增加，晶粒尺寸增大；合金的强度下降，塑性先增加后下降。材料的应变硬化行为呈现3阶段硬化。在变形过程中，奥氏体中发生平面滑移，铁素体中发生波状滑移。随着变形量的增加，在奥氏体中形成不同方向的滑移带，铁素体中形成胞状结构。钒的添加可同时提高材料的强度和塑性。     

Influencing parameters on elastic modulus of steels

An optimised balance between weight and stiffness of a car component is achieved when the selected material exhibits an increased ratio between elastic modulus and density. The elastic modulus of steel decreases progressively with increasing temperature due to the thermal activation of lattice vibrations. Since the elastic modulus of metals is related to their lattice constants, austenitic steels are expected to exhibit higher elastic moduli than ferritic steels because of their higher packing density. However, the coupling of electron spin moments due to the ferromagnetic character of bcc steels results in higher elastic modulus of ferritic steels at temperatures below the Curie temperature. An increase in elastic modulus in selected loading directions can be realised by properly adjusted crystallographic textures. However, no examples were found where the maximum elastic modulus exceeds 225 GPa in bcc steels with pronounced crystallographic textures. Alloying elements decrease the elastic modulus with increasing alloying content. Known exceptions from this rule are the elements Re, Co and Cr. The elastic modulus of steel can be increased significantly by particles of high elastic modulus. Finally, it is reduced by plastic deformation because of the increased dislocation density. This negative effect can be balanced by subsequent heat treatments.

On obtient une balance optimisée entre le poids et la rigidité d′une piéce d′automobile lorsque le matériau choisi exhibe une augmentation du rapport entre le module d′élasticité et la densité. Le module d′élasticité de l′acier diminue progressivement avec l′augmentation de la température à cause de l′activation thermique des vibrations du réseau. Puisque le module d′élasticité des métaux est relié à leurs constantes de réseau, on s′attend à ce que les aciers austénitiques exhibent des modules d′élasticité plus élevés que ceux des aciers ferritiques parce qu′ils possédent une plus grande densité de tassement. Cependant, le couplage des moments du spin électronique, dû au caractére ferromagnétique des aciers bcc, résulte en un module d′élasticité plus élevé des aciers ferritiques à des températures plus basses que la température de Curie. On peut augmenter le module d′élasticité dans des directions choisies de charge en ajustant correctement les textures cristallographiques. Cependant, nous n′avons pas trouvé d′exemples où le module d′élasticité maximum excédait 225 GPa dans les aciers bcc ayant des textures cristallographiques prononcées. L′augmentation de la teneur en éléments d′alliage diminue le module d′élasticité. Les éléments Re, Co, et Cr font exception à cette règle. On peut augmenter significativement le module d′élasticité de l′acier à l′aide de particules à module d′élasticité élevé. Finalement, le module d′élasticité est réduit par déformation plastique à cause de l′augmentation de la densité de dislocation. On peut balancer cet effet négatif au moyen de traitements thermiques subséquents.     

Fe-23Mn-xAl-0.7C低密度钢中非金属夹杂物形成机理

 为了研究Fe-23Mn-xAl-0.7C(x=0.87～6.76)低密度钢中非金属夹杂物形貌特征及形成机理,通过SEM-EDS检测了钢中夹杂物形貌和成分,并借助INCA Feature夹杂物自动分析软件分析了钢中夹杂物尺寸分布、数量密度和面积分数等参数。研究发现,低密度钢中夹杂物尺寸以1～5 μm为主。w([Al])为0.87%时,钢中主要夹杂物为MnS、MnO、Al₂O₃和Al₂O₃-MnS,夹杂物数量较少,但尺寸大于7 μm的夹杂物所占比例较大,平均尺寸为3.45 μm;w([Al])为3.28%时,主要夹杂物为AlN、Al₂O₃、MnS以及AlN-MnS、AlN-Al₂O₃-MnS复合夹杂物,外包裹MnS尺寸较小,小尺寸夹杂物居多,平均尺寸为2.63 μm;w([Al])为6.76%时,钢中夹杂物以AlN或AlN-MnS为主,且AlN夹杂呈聚集状,夹杂物平均尺寸为2.93 μm。此外,通过FactSage 7.3热力学计算讨论了Fe-23Mn-xAl-0.7C低密度钢中夹杂物析出时机及演变过程,为试验结果提供理论解释。