钢的热处理组织分析：第三讲 钢的各类热处理组织形态（二）

4 马氏体及铁素体或碳化物组织这类组织对亚共析钢来说是马氏体及铁素体,对过共析钢来说是碳化物及马氏体组织.马氏体和铁素体组织.因铁素体的来源不同,其形态也不同.若淬火温度低于Ac_3/高温下有未溶铁素体,冷却时按图1中V_1;的速度冷却.奥氏体完全转变为马氏体,铁素体被保留下来成为组织组成物之一.若加热温度高于Ac_3,高温组织为单相奥氏体,冷却时以图1中V_4的速度冷却,也就是生产中有时采用的预冷淬火,即出炉后在空气中预冷一定时间,再淬入介质中快冷(相当于图1中V_5).但因在空气中预冷时间过长,使淬入介质之前已从奥氏体中析出铁素体,再淬入介质后剩余的奥氏体完全转变为马氏体.由于铁素体形态不同,所以这类组织可能有图4所示的三种形态.第一种是如图4a所示的块状铁素体加马氏体,铁素体是未溶的白色块状,其分布仍然保留淬火前沿轧向呈带状分布.第二种如图4b所示的条网状铁素体加马氏体.由于冷却不足,淬火时首先沿奥氏体晶界析出呈网状分布的铁素体,冷至M_s点时,过冷奥氏体发生马氏体转变,生成低碳马氏体.在b图中铁素体为白色网条状,明显可见沿奥氏体晶界分布的特点;图中还有极少量的针状铁素体.第三种是兼有前两种形态的铁素体,即既有未溶的块状铁素体,又有析出的条网状铁素体,如图4c 所示.图     

HSLA钢连续冷却过程的相变与组织研究

在Gleeble-1500热模拟试验机上研究了20SiMn3NiA钢在不同连续冷却条件下相和组织变化,用热膨胀法测定了该钢的连续冷却转变曲线(动态CCT曲线)。研究结果表明,20SiMn3NiA钢中的Mn、Ni、Si等合金元素能有效地阻止铁素体和珠光体的形成,故20SiMn3NiA钢的过冷奥氏体连续冷却转变曲线只有马氏体和贝氏体相变区。当临界冷却速度大于1℃/s时,20SiMn3NiA钢就可以获得板条状马氏体组织,且随着冷却速度的增大,马氏体组织变得越来越细。与静态CCT曲线相比,形变使动态CCT曲线的Ms点升高,奥氏体稳定性降低,形变细化了马氏体和贝氏体组织,使20SiMn3NiA钢在1℃/s的冷却速率下产生较高的强度。     

800MPa级冷轧耐候双相钢连续冷却相变及组织性能研究

为了探索一种800 MPa级冷轧耐候双相钢的连续冷却转变规律及退火后组织性能变化,利用For-master-FⅡ全自动相变仪及连续退火模拟实验机,进行了连续冷却转变(CCT)曲线的测定及连续退火实验.结果表明:实验钢的过冷奥氏体在很低的冷却速度(0.5℃/s)下即可发生马氏体转变,而珠光体转变较少.当冷速为80℃/s时,仅发生马氏体转变;退火后实验钢显微组织中的马氏体呈带状分布,经最优工艺退火后实验钢的显微组织为多边形铁素体(79%)+块状马氏体(16%)+细小的残余奥氏体(5%),残余奥氏体主要分布于马氏体晶粒内部或铁素体的晶界处;实验钢屈服强度为387 MPa,抗拉强度为863 MPa,延伸率为18%,强塑积达到15534.     

Q460C钢的连续冷却转变曲线

研究了Q460C钢连续冷却过程中奥氏体转变过程以及转变产物的组织变化,为制定生产工艺提供参考依据。由Q460C钢的连续冷却转变曲线(CCT图)和不同冷却速率的显微组织可知,当冷却速率较低时,形成粗大的块状铁素体和珠光体;当冷却速率大于3℃/s时出现贝氏体,形态似针状铁素体,其形成温度在450~600℃;当冷却速率大于15℃/s时,发生马氏体转变,马氏体的转变点约为350℃。     

一种汽车用微合金非调质钢的连续冷却转变

测定了一种汽车用微合金非调质钢的过冷奥氏体连续冷却转变曲线,研究了冷却速率对相变组织及显微硬度的影响。结果表明：试验钢的临界点A_c3为838℃,A_c1为732℃;当冷却速率小于0.2℃/s时,试验钢的连续冷却转变产物为铁素体、珠光体和贝氏体;当冷却速率为0.2℃/s时,转变产物中出现马氏体;当冷却速率为5℃/s时,铁素体、珠光体消失,转变产物为贝氏体和马氏体;随着冷却速率的增大,马氏体含量逐渐增多,贝氏体含量逐渐减少,甚至完全消失;当冷却速率增大至20℃/s时,转变产物均为马氏体;随着冷却速率的增大,试验钢的显微硬度呈先快速增长,后增长速率变缓的趋势。     

加热速度对T91铁素体耐热钢奥氏体形成的影响

采用高精度差分膨胀仪对不同加热速度(10~6000 K/min)下T91铁素体耐热钢的奥氏体形成动力学规律进行了系统研究.研究表明:加热速度显著影响T91钢的奥氏体形成开始温度Ac1、结束温度Ac3、相变速率及淬火后的组织.加热速度愈大,Ac1和Ac3温度愈高,奥氏体相变速率愈快,奥氏体形成温度区间愈窄;相对较慢和较快的加热速度对淬火后的组织都有不利的影响.     

CLAM钢焊接热影响区连续冷却过程相变规律

采用Gleeble1500热模拟机,物理模拟中国低活化马氏体(CLAM)钢焊接热影响区粗晶区(CGHAZ)的冷却过程,结合组织观察、Thermo-calc热力学软件计算和硬度测试等手段分析了冷速ωc对CGHAZ的组织演变及硬度的影响,并绘制了CLAM钢的SH-CCT图。结果表明:CLAM钢的CGHAZ中过冷奥氏体仅发生低温板条马氏体(LM)及先共析铁素体(α铁素体)转变。0.25℃/s为CGHAZ过冷奥氏体发生完全LM相变的临界冷速。当ωc>0.25℃/s时,CGHAZ的组织除LM外,还含有少量的δ铁素体,δ铁素体是δ→γ相变阶段转变不充分而残留至室温的组织,在该冷速范围内粗晶区的组织形态变化不明显。当ωc<0.25℃/s时,由于发生γ→α转变,CGHAZ的组织为α铁素体及LM的混合组织,随着冷速的降低,α铁素体含量增加;当ωc=0.04℃/s时,CGHAZ的组织已完全转变为α铁素体和碳化物的混合组织。     

Q345钢奥氏体连续冷却转变曲线(CCT图)

研究了Q345钢连续冷却过程中奥氏体转变过程及转变产物的组织和性能,为制定生产工艺提供参考依据.利用膨胀法结合金相-硬度法,得到不同冷却速度连续冷却时的膨胀曲线和相应的金相组织及硬度,用DTA法及膨胀法测定其临界点Ac1、Ac3以及Ms,获得了Q345钢的连续冷却转变曲线(CCT图).由CCT图和不同冷却速度的显微组织照片可知,当冷却速度比较低时,形成较粗大的块状铁素体和珠光体,当冷却速度大于0.5℃/s时出现贝氏体,形态似针状铁素体,其形成温度在450~600℃左右,当冷却速度大于20℃/s时,发生马氏体转变,马氏体转变点约为400℃.     

65Mn钢奥氏体连续冷却转变曲线(CCT图)

利用膨胀法结合金相--硬度法,在Gleeble-1500热模拟机上测定了65Mn钢的临界点Ar1、Ar3、Ac1和Ac3以及Ms;测定了该钢在不同冷却速度下连续冷却时的膨胀曲线,获得了该钢的连续冷却转变曲线(CCT曲线);研究了65Mn钢连续冷却过程中奥氏体转变过程及转变产物的组织和性能,大致确定了避免网状铁素体、贝氏体以及魏氏组织铁素体的冷却速度,找出了生产65Mn钢盘条的控冷速度范围,为生产实践和新工艺的制定提供了参考依据.     

冷却速度对T91相变速度和产物的影响

本文研究了T91钢冷却过程中,不同冷却速度（10k/min（200k/min）对相变速度和产物的影响。研究表明不同的冷却速度生成的组织差别较大,在较低速冷却下（10k/min和30k/min）的组织为较多的先共析铁素体和板条马氏体,中速冷却（30k/min和50k/min）基本都为板条马氏体,在较高速冷却过程中（100k/min和200k/min）组织中除了板条马氏体还出现了片状马氏体,另外冷却速度还影响了相变开始点和相变速度。     

Effects of Austenite Stabilization on the Onset of Martensite Transformation in T91 Steel

The influences of thermal stabilization of austenitic on the onset temperature for a martensite transformation in T91 ferritic heat-resistant steel were studied by high-resolution differential dilatometer. The phase transformation kinetic information was obtained by adopting lever rule from the recorded dilatometric curves. The results show that an inverse stabilization, featured by the damage of ＂the atmosphere of carbon atoms＂ and the increase of the starting temperature for martensite transformation takes place when the T91 ferritic steel is isothermally treated above the Ms point, and it becomes strong with increasing the holding time. While the continued temperature for martensite transformation decreases gradually when isothermally holding at a temperature below Ms point. The observed inverse stabilization behavior could be attributed to the relatively high temperature of Ms point in the explored T91 ferritic heat-resistant steel.     

Effect of deformation of austenite and cooling rates on transformation microstructures in a Mn–Cr gear steel

The effect of austenite deformation and cooling rates on continuous cooling transformation microstructures for a Mn–Cr gear steel were investigated using a Gleeble 1500 thermomechanical test system. The experimental results show that the deformation of austenite promotes the formation of proeutectoid ferrite and pearlite, leading to the increase of critical cooling rate of proeutectoid ferrite plus pearlite microstructure. The deformation enhances the stability of austenite against bainite transformation, which results in an increase in amount of martensite/austenite (M/A) constituent with deformation at some cooling rates studied. Moreover, cooling rate also affects amount of M/A constituent. With decrease of cooling rate, amount of M/A constituent increases at first, but decreases subsequently till disappears eventually.     

Effect of austenite microstructure and cooling rate on transformation characteristics in a low carbon Nb-V microalloyed steel

Deformation dilatometry has been used to simulate controlled hot rolling followed by cooling of a Nb-V low carbon steel, looking for conditions corresponding to wide austenite grain size distributions prior to transformation. Recrystallization and non-recrystallization deformation schedules were applied, followed by controlled cooling at rates from 0.1 °C/s to about 200 °C/s, and the corresponding continuous cooling transformation (CCT) diagrams were constructed. The resultant microstructures ranged from polygonal ferrite (PF) and pearlite (P) at slow cooling rates to bainitic ferrite (BF) accompanied by martensite (M) for fast cooling rates. Plastic deformation of the parent austenite accelerated both ferrite and bainite transformations, displacing the CCT curve to higher temperatures and shorter times. However, it was found that the accelerating effect of strain on bainite transformation weakened as the cooling rate diminished and the polygonal ferrite formation was enhanced. Moreover, it was found that plastic deformation had different effects on the refinement of the microstructure, depending on the cooling rate. An analysis of the microstructural heterogeneities that can impair toughness behavior has been done.     

30CrNi3MoV低合金超高强钢中的马氏体相变

通过对马氏体的显微组织进行分析,并结合线膨胀试验得到的相变动力学信息研究了30CrNi3MoV低合金超高强钢中的马氏体相变特征.结果表明:淬火冷却30CrNi3MoV钢的相变产物包括低碳板条状和高碳针状两种马氏体形态,两者的形成在动力学曲线中截然分开.板条马氏体形成于Ms以下的较高温(310℃～260℃),相变过程中发生了碳的重新分配,造成富碳奥氏体微区的形成;高碳针状马氏体形成于Ms以下的较低温(260℃～170℃),由富碳奥氏体微区转变而成.板条马氏体形成速率远高于针状马氏体.     

Phase transformation and mechanical behaviour of thermo-mechanically controlled processed high-strength multiphase steel

A novel low-alloy high-strength steel [Fe–0.20C–1.65Mn–1.40Si–1.50Al–1.30Cu–1.05Ni–1.07Co (wt%)] has been thermo-mechanically processed with a finish rolling temperature of 850 °C, followed by air cooling and water quenching in order to obtain a good combination of strength and ductility. Phase transformations of the above steel at different cooling rates have been studied and continuous cooling transformation (CCT) diagram has been constructed using data, obtained from dilatometric study. The phase field of CCT diagram indicates microstructure changes from a mixture of ferrite and bainite to fully martensite accompanied with the enhancement of hardness with increasing cooling rate. The microstructural investigation at lower cooling rate (≤5 °C/s) suggests the possibility of achieving pearlite-free microstructure by direct air cooling from the austenite region. Directly air-cooled steel has demonstrated primarily ferrite–bainite microstructure, which shows attractive tensile strength (>1050 MPa) and ductility (>15 %). On the other hand, directly water-quenched steels reveal predominantly lath martensitic microstructure with high dislocation density which exhibits higher tensile strength (>1600 MPa) and lower ductility (~12 %). The multiple stages of strain hardening behaviour of the investigated steel under different cooling conditions have been examined with respect to microstructural evolution.     

Investigation on decomposition behavior of austenite under continuous cooling in vanadium microalloyed steel (30MSV6)

In the present study, investigations are focused on microstructural evolution and the resulting hardness during continuous cooling transformation (CCT) in a commercial vanadium microalloyed steel (30MSV6). Furthermore, the effects of cooling rate and austenite grain size (AGS) on CCT behavior of the steel have been studied by employing high-resolution dilatometry. Quantitative metallography accompanied with scanning electron microscopy (SEM) has efficiently confirmed the dilatometric measurements of transformation kinetics and austenite decomposition products. A semi-empirical model has been proposed for prediction of microstructural development during austenite decomposition of the steel and the resultant hardness. The model consists of 8 sub-models including ferrite transformation start temperature, ferrite growth, pearlite start temperature, pearlite growth, bainite start temperature, bainite growth, martensite start temperature and hardness. The transformed fractions of ferrite, pearlite and bainite have been described using semi-empirical Johnson–Mehl–Avrami–Kolmogorov (JMAK) approach in combination with Scheil's equation of additivity. The JMAK rate parameter for bainite has been formulated using a diffusion-controlled model. Predictions of the proposed model were found to be in close agreement with the experimental measurements.     

Effect of continuous-cooling transformation structure on mechanical properties of 0.4C-Cr-Mo-Ni steel

Commercially available 0.4C-Cr-Mo-Ni steel was studied to determine the effects on its mechanical properties of various microstructures produced by continuous-cooling transformation after austenitization. A good combination of strength and notch toughness was obtained independently of test temperatures (293 and 193 K) when the steel was austenitized at 1173 K and then continuously cooled at an average rate of 3.1 K s^–1 (expressed as the average cooling rate from 823 to 573 K) before final rapid cooling. The microstructure of the steel consisted of a mixed structure of martensite and 10–15 vol% lower bainite, which appeared in acicular form in association with the martensite. Slower cooling had a detrimental effect on the mechanical properties of the steel; the microstructure of this steel consisted of a mixed structure of martensite and upper bainite, which appeared as masses in the matrix. As the average cooling rate increased, the lath size and internal stringer-carbide size in the upper bainite were larger, and retained a somewhat increased austenite content.