Effect of Strain Rate on the Ferrite Grain Refinement in a Low Carbon Nb-Ti Microalloyed Steel during Low Temperature Deformation

Grain refinement is one of the effective methods to develop new generation low carbon microalloyed steels possessing excellent combination of mechanical properties. The microstructural evolution and ferrite grain refinement at the deformation temperature of 865℃, above Ar3, with different strain rates were investigated using single pass isothermal hot compression experiments for a low carbon Nb-Ti microalloyed steel. The physical processes that occurred during deformation were discussed by observing the optical microstructure and analyzing the true stress-true strain responses. At strain rates of 0.001 and 0.01s^-1, there is no evidence of work hardening behavior during hot deformation and strain-induced transformation （SIT） leads to dynamic flow softening in flow curves. Optical microscopy observation shows that ultrafine and equiaxed ferrite with grain sizes of 2μm can be obtained by applying deformation with strain rate of 0.1 s^-1 due to SIT just after deformation. Furthermore, increasing the strain rate from 0.001 to 0.1 s^-1 reduces both the grain size of the equiaxed ferrite and the amount of deformed ferrite.

Characteristics of Strain-Induced Ferrite in Low Carbon Steel

The strain-induced ferrite formed under different conditions was observed with SEM and optical microscope.The nucleation sites of strain-induced ferrite include grain boundary,grain inside,deformed band and annealing twin boundary.The shapes of the ferrite accordingly are equiaxed irregular polygonal,strip-shaped and acicular.

Investigation into the stress-strain curves of deformation-induced ferrite transformation in a low carbon steel

A series of tests of deformation-induced ferrite transformation （DIP-T） in a low carbon steel were carried out by the Gleeble-3500 hot simulation machine at a temperature range of Ae3-Ar3. The overall stress-strain curves during DIFT can be divided into three typical types： ＂double-humped＂,＂ single-humped＂ and ＂transitional＂. The peaks exhibited in the curve are involved with deformation-induced transformation which happened in grains or at the grain boundaries. According to the stress-time curve and strain-time curve, strain capacity dramatically postponed the strain-induced transformation, which leads to the start of the transformation right ahead of the finish of deformation and the majority of the ferrite transformation process mainly happened after the deformation. Deformation-induced transformation is a metadynamic transformation process with dynamic nucleation.

Austenite Recrystallization and Controlled Rolling of Low Carbon Steels

The dynamic recrystallization and static recrystallization in a low carbon steel were investigated through single-pass and double-pass experiments. The results indicate that as the deformation temperature increases and the strain rate decreases, the shape of the stress-strain curve is changed from dynamic recovery shape to dynamic recrystallization shape. The austenite could not recrystallize within a few seconds after deformation at temperature below 900 ℃. According to the change in microstructure during deformation, the controlled rolling of low carbon steel can be divided into four stages： dynamic recrystallization, dynamic recovery, strain-induced ferrite transformation, and rolling in two-phase region. According to the microstructure after deformation, the controlled rolling of low carbon steel can be divided into five regions： non-recrystallized austenite, partly-recrystallized austenite, fully-recrystallized austenite, austenite to ferrite transformation, and dual phase.

The micro structure of high carbon low alloy steel for easy drawing

For better processing performance of high carbon low alloy steel wire rod,an investigation about the influence of cementite lamellar spacing on wire 'easy drawing' performance is completed.It is pointed out that too thin cementite lamellar spacing(<80 um) reduces the strain hardening level of wire drawing, and reduce the torsion performance of drawn wire at same time.For the wire or wire rod from industrial production,compared with the micro-structure with troostite,the micro-structure with sorbite or sorbite mixed with pearlite is more suitable to the drawing process with high reduction ratio.

Influence of prior austenite grain size on the critical strain for completion of DEFT through hot compression test

A low carbon steel was used to determine the critical strain εc for completion of deformation enhanced ferrite transformation （DEFT） through a series of hot compression tests. In addition, the influence of prior austenite grain size （PAGS） on the critical strain was systematically investigated. Experimental results showed that the critical strain is affected by PAGS. When γ→α transformation completes, the smaller the PAGS is, the smaller the critical strain is. The ferrite grains obtained through DEFT can be refined to about 3 μm when the DEFT is completed.

Characterizations of Dynamic Strain-induced Transformation in Low Carbon Steel

Dynamic strain-induced transformation of the low carbon steel Q（235） at 770℃ and 850℃ leads to fine ferrite grains. The microstructure characterization and mechanism of the fine ferrite grain were studied by scanning electron microscopy （SEM）, transmission electron microscopy （TEM） and electron backscattered diffraction （EBSD） technique. The results show that strain-induced microstructure is the mixed microstructure of ferrite and pearlite, with cementite randomly distributed on ferrite grain boundaries and the grains interiors. EBSD images of grain boundaries demonstrate that high angle grain boundaries （HAGBs） are dominant in both of the deformation induced microstructures occurring below and above A（e3） , with only a few low angle grain boundaries （LAGBs） existing in the grain interiors. It implies that the dynamic strain-induced transformation （DSIT） happens above and below A（e3） temperature and has the same phase transition mechanisms. The refinement of ferrite is the cooperative effect of DSIT and continuous dynamic recrystallization （CDRX） of ferrite. Besides, DSIT is deemed as an incomplete carbon diffusion phase transition through the analysis of microstructure and the previous simulated results. The strengths of the Q（235） steel with refined ferrite and pearlite structure get doubled than the initial state without treated by DSIT and the residual stress in the refined structure is partly responsible for the ductility loss.

Study on Microstructure and Performance of Advanced Bush Strip

The strain induced ferrite formed under different conditions was observed with SEM and optical microscope. The nucleation sites of strain induced ferrite include grain boundary, grain inside, deformed band and annealing twin boundary. The shapes of the ferrite accordingly are equiaxed irregular polygonal, strip shaped and acicular.

Strain gradient induced grain refinement far below the size limit in a low carbon hypoeutectoid steel(0.19 wt%C)via pipe inner surface grinding treatment

A low carbon hypoeutectoid steel(0.19 wt%C)with proeutectoid ferrite and pearlite dual-components was subjected to surface plastic deformation via pipe inner surface grinding(PISG)at room temperature.The deformation microstructures for each component were systematically characterized along depth,and the patterns of structural evolution toward nanometer regime as well as the governing parameters were addressed.Proeutectoid ferrite grains were refined down to 17 nm,and the pattern covering a length scale of 4–5 orders of magnitude from micron-to nanometer-scale follows:formation of cellular dislocation structure(CDS),elongated dislocation structure(EDS),ultrafine lamellar structure(UFL)and finally the nanolaminated structure(NL).The pearlite experiences the deformation and refinement,and finally the transforming the ultrafine pearlite(UFP)into nanolaminated pearlite(NLP)with the ferrite lamellae as thin as 20 nm.Refinement for both UFL(UFP)and NL(NLP)can be realized via forming novel extended boundaries within ferrite lamellae.A critical lattice curvature of~2.8°is required for forming such extended boundary,corresponding to a minimum strain gradient of 0.25μm^(-1)for a 100 nm-thick lamella.Refinement below size limit(expressed by lamellar thickness d_Tin nm)is correlated with the strain gradient(χ,inμm^(-1))by:d_T=12.5/x.Refinement contributions from strain gradient caused by PISG processing and material heterogeneity were discussed.

奥氏体转变温度以上变形时应变速率对低碳钢动态软化行为的影响

利用Gleeble-1500热模拟试验机,将一低碳微合金钢在Ac3温度以上(950℃)进行了4种不同的应变速率(10、7、3、1 s^(-1))的压缩变形,然后淬火处理。对高温变形的应力应变曲线用双微分法进行变换,发现材料变形过程中主要有两种软化机制,分别为动态相变和动态再结晶,随变形速率的增加,材料发生软化的两个临界应力呈线性升高的趋势;两个临界应变则随应变速率变化不大。用金相显微镜观察观察了材料淬火后的金相组织,发现材料内的Widmanstätten铁素体板条宽度随应变速率的增加而逐渐变细,多边形铁素体的数目随应变速率的增加而增加;Widmanstätten铁素体板条一般为平行或垂直关系,而垂直关系的Widmanstätten铁素体板条并不呈现严格的直角,而是偏离一定的角度。

基于热模拟试验机的大试样平面应变技术

使用热模拟试验机对大试样低碳钢进行了平面应变压缩热模拟试验,并对其各道次应力-应变曲线及相变温度进行分析,获得了低碳钢变形区的显微组织演变规律。通过调整热模拟试验机的参数,确保大试样在升温、保温和降温过程中保持温度稳定。结果表明:在保温阶段,试样的均温区尺寸(长度×宽度×高度)为30 mm×30 mm×20 mm,温差约为20℃,满足平面应变压缩试验对试样均温性的要求;压缩变形后试样的宽展较小,试样中间区域的显微组织相对均匀,力学性能较稳定。采用热模拟试验机的平面应变技术可以较好地模拟低碳钢压缩变形时的平面应变状态,实现同时分析材料的显微组织和力学性能。

低碳钢应变诱导铁素体相变发生的温度条件

用Gleeble 1500热模拟实验机进行了低碳钢不同温度下变形后自动落入水中的淬火实验,组织分析表明铁素体的组织形态在一定温度下发生了明显变化 结合变形后冷却过程膨胀曲线的测量结果,确定实验条件下应变诱导相变发生的上限温度为830℃左右.利用喷水淬火法试样冷却速度分布不均匀的现象,确定低碳钢变形后抑制铁素体析出的临界冷却速度为400℃/s,并采用此方法确定了应变诱导相变的上限温度.结合实验结果对应变诱导铁素体相变机制及发生的温度条件进行了分析.

低碳钢热变形奥氏体的再结晶行为

对热变形奥氏体的再结晶动力学和微观组织演变进行了模拟计算,对晶粒尺寸的模拟值和实测值作了比较,分析了化学成分对动态再结晶率的影响以及残余应变与变形温度的关系。结果表明:在温度较高、应变速率较低的条件下容易发生动态再结晶,随着变形温度的降低,发生动态再结晶的几率减小,而静态再结晶在前几道次进行得比较充分,随后进行得不充分,增加碳和锰的含量可以促进动态再结晶的发生,残余应变随变形温度的降低而增大,晶粒尺寸的模拟值和实测值吻合较好,表明所选用的模型有一定的参考价值。

低碳钢奥氏体晶粒控制对应变强化相变的影响

研究了在温度过冷条件下，名义变形为 ５０％（应变为－０．６９）；应变速率为 １ｓ－１；形变温度为 ８００－７４０ ℃时，低碳钢相交前奥氏体晶粒尺寸（平均直径为 ４４－７ μｍ）对应变强化相支铁素体转变量及铁素体晶粒大小的影响形变前奥氏体晶粒小的铁素体转变量增加，相交完成后细小铁素体晶粒分布较均匀；形变前奥氏体晶粒粗大时，形变后铁素体转变不完全，铁素体晶粒粗大且不均匀．

低碳钢控制轧制的温度范围及组织变化

以碳 (质量分数 ) 0 0 5 7% ,锰 (质量分数 ) 0 91%的低碳钢为研究对象 ,在Gleeble 15 0 0热模拟实验机上利用喷水淬火法确定了应变诱导相变发生的上限温度Ad3·根据热变形过程中组织变化的主要过程将低碳钢的控制轧制分为 3个阶段 :Ad3以上、Ar3～Ad3之间以及Ar3以下·在 3个温度范围内进行了不同参数的压缩实验 ,通过组织分析研究了变形过程中的组织变化·结果表明 ,在Ad3以上 ,变形过程中主要发生奥氏体的动态再结晶过程 ;Ar3～Ad3之间 ,变形过程中有应变诱导铁素体析出 ,且随着变形温度的降低、变形量的增加及变形速率的降低 ,铁素体量增加 ;在Ar3以下 ,先共析铁素体发生动态再结晶 ,奥氏体晶界和晶内有大量铁素体析出·

应变诱发铁素体相变对低碳钢晶粒细化的影响

研究了在奥氏体低温区变形时显微组织的变化 ,并测试了其变形抗力。结果表明 :在 Ar3 以上温度变形会产生应变诱发铁素体相变 ,使变形抗力下降。通过降低变形温度 。

低碳钢应变诱导铁素体相变研究中的淬火问题

在 Ｇｌｅｅｂｌｅ－１５００热模拟实验机上对 ＳＳ４００钢进行厂不同温度下的单道次变形实验，对变形后采用喷水和自动落水两种淬火方法的效果进行了对比． 通过对不同变形温度以及试样不同部位的组织分析研究了先共析铁素体的析出规津， 结合不同温度变形后相变点测定的实验结果，确定了应变诱导铁素体相变的上限温度，探讨了应变诱导相变的机制 ，喷水淬火时，试样下同部位冷却速度相差大，不同部位的组织差别也大，冷却速度慢，等轴铁素体多，增加冷却速度，铁素体形态变为包含晶界非整形和魏氏组织侧片铁素体的复杂组织，铁素体量越来越少，自至完全为马氏体，变形温度在８００℃以下，铁素体主要为分布在奥氏体晶界并呈等轴状，应变诱导相变的上限温度为 Ａｒ３与变形温度重合的最高温度，一般在未变形试样的 Ａｒ３以上６０℃左右．

低碳铁素体贝氏体复相钢的拉伸应力-应变曲线分析

对一种低碳钢进行了控轧控冷实验,获得了具有铁素体和贝氏体的复相组织。通过室温静态拉伸实验、光学显微镜等手段对复相钢进行了表征。研究了在拉伸速度恒定条件下的硬化行为。并利用Crussard-Jaoult分析方法对应力应变曲线进行分析。结果表明,具有铁素体和贝氏体组织的低碳钢具有较高的强度和较高的初始加工硬化指数,应变硬化指数随着真应变的提高呈先升高后下降的趋势,应变硬化速率随应变的升高呈下降的趋势。均匀分布的贝氏体有助于提高实验钢的应变硬化能力。

基于梯度塑性理论的单向拉伸低碳钢试样颈缩分析

采用非局部的梯度塑性理论 ,得到了断面收缩率及颈缩区内部不同位置直径的解析解。应变软化越严重 ,颈缩程度越大。在颈缩区域中部 ,半径最小。在颈缩区域内轴向拉应力分布是不均匀的 ,在颈缩区域中部 ,其值最大 ,而在颈缩区域边缘 ,其值最小。随着流动拉应力的降低 ,颈缩区域中部的真应力持续增加。在应变软化过程中 ,断面收缩率持续增加 ,但增加的速度越来越慢。

Nb微合金低碳钢表层超细晶中厚板的研制

应用中间坯加速冷却―轧制―轧后加速冷却工艺轧制的10 mm表层超细晶(1～5μm)Nb微合金高强度钢板,超细晶层厚度为0.5～2.0 mm,其屈服强度达到640 MPa,抗拉强度740 MPa,伸长率达到27%,–40℃冲击吸收功大于130 J。利用光学电镜、扫描电镜和透射电镜观察分析组织,得到如下结论:铁素体晶粒超细化的机制是过冷奥氏体应变诱导铁素体相变,先共析和应变诱导的铁素体动态再结晶;强化机制为细晶强化,Nb析出物的弥散析出强化,位错及亚结构强化;在实施中间坯加速冷却前通过再结晶区轧制得到细化的奥氏体晶粒,或未再结晶区轧制获得形变奥氏体晶粒,或在中间坯加速冷却后增大轧制压缩比,和降低轧后加速冷却的终冷温度均有利于获得表层超细晶粒,同时增大整个厚向超细晶粒比例。