CSP热轧TRIP 600钢的连续冷却相变行为

利用Thermecmastor-Z型热模拟试验机、Formastor-F型相变仪,结合光学显微镜、扫描电子显微镜及显微硬度计等设备系统研究了CSP热轧TRIP 600钢的连续冷却相变行为,获得了试验钢的动态及静态CCT曲线,探讨了形变和冷速对其相变行为的影响。研究结果表明:随着冷速的增加,试验钢中铁素体转变温度逐渐降低,体积分数不断减少,其转变温度范围为480~716℃;珠光体含量则先增加后减少,转变温度范围为519~647℃。当冷速大于2℃/s时,试验钢中已出现贝氏体转变,其含量随冷速的增加先增大后减小,转变温度范围为451~533℃。试验钢经变形后,钢中铁素体、珠光体及贝氏体转变温度范围往左上方移动,分别为550~760、539~708和478~550℃,而且相同冷速下钢中组织更加细小。此外,变形也会提高奥氏体的机械稳定性,抑制马氏体转变,使得马氏体开始转变温度Ms由418℃降至360℃。     

工艺参数对耐蚀钢12CuCrNiV组织与性能的影响

采用热力模拟试验机、光学显微镜、显微硬度计研究了耐蚀钢12CuCrNiV在不同冷却速率下的连续冷却组织转变规律,并绘制其CCT曲线,同时研究了形变温度和冷却速度对耐蚀钢热变形后的组织和硬度的影响规律。结果表明:连续冷却转变情况下,耐腐蚀钢在冷速小于15℃/s时,有铁素体转变;冷速小于1℃/s时,有珠光体转变;冷速在0.5~20℃/s之间时,有贝氏体转变。控制冷速在5~15℃/s可得到铁素体和贝氏体复相组织。随变形温度的降低,试验钢形变过程中形变诱导铁素体相变现象显著,且伴随有M/A岛生成;随冷却速度的增高,形变诱导相变现象减弱,M/A岛数量减少。与连续冷却试验相比较,形变诱导析出现象明显,其硬度增量为40~50HV,形变可使试验钢的析出向更高冷速移动。     

控冷冷速对高性能桥梁钢组织和力学性能的影响

 为了使控轧控冷工艺生产的高性能Q500qE桥梁钢具有较低的屈强比和良好的韧性,采用Gleeble-3800试验机模拟了试验钢不同冷速控冷工艺,研究了冷速对组织和力学性能的影响。结果表明：5~25 ℃/s冷却速率下形成针状铁素体、粒状贝氏体铁素体和少量弥散M-A岛构成的多相组织。随冷速增加,铁素体晶粒细化,M-A岛尺寸减小;强度和屈强比提高,冲击功先升高后降低。试验钢满足力学性能要求的控冷冷却速率范围是15~20 ℃/s。     

贝氏体型非调质钢SBL的连续冷却转变

研究获得了Mn－B系低碳贝氏体型非调质钢SBL热变形奥氏体的连续冷却转变曲线。试验结果表明,本试验用钢热变形奥氏体不发生先共析铁素体析出临界冷却速度为1．5℃／s;冷却速度在1．5－7℃／s范围内可得到贝氏体组织;当冷速大于7℃／s时,不再有贝氏体生成,室温组织为马氏体和残余奥氏体。     

热形变和钒微合金化对高碳钢组织转变的影响

通过在Gleeble1500热模拟试验机上的热形变和冷却试验,研究了热形变及钒微合金化对高碳钢连续冷却后显微组织及硬度的影响。研究结果表明：未形变的含钒试验钢在5和9℃/s冷速下出现了中低温组织贝氏体和马氏体,950℃变形后的含钒钢,在同样冷速下相变后得到的组织全为珠光体。随钒含量的增加,珠光体转变后的片层间距变小,硬...     

压力容器用14Cr1MoR钢奥氏体连续冷却转变曲线

利用膨胀仪测定了14CrlMoR钢(/%:0.01C,0.66Si,0.80Mn,0.006P,0.003S,1.72Cr,0.31Mo,0.01Nb)的临界点及连续冷却转变曲线并研究了冷却速度对试验钢的组织及显微硬度的影响。结果表明,当冷却速度为0.1~1℃/s时,试验钢的转变组织为铁素体和珠光体;2~5℃/s时,试验钢得到铁素体、珠光体以及少量粒状贝氏体的混合组织;10℃/s时,试验钢组织为铁素体和粒状贝氏体;15~20℃/s时为板条贝氏体组织;25~50℃/s时,该钢得到板条贝氏体和马氏体的混合组织。     

钒微合金化低碳贝氏体钢的连续冷却相变特性

 采用热膨胀法测定6种不同成分低碳贝氏体钢的连续冷却转变(CCT)曲线。CCT曲线表明,加入微量硼能使含钒低碳贝氏体钢在大于03℃/s的冷速下获得贝氏体组织,而V-N微合金化的低碳贝氏体获得全贝氏体的临界冷速要高于V-B钢,且贝氏体转变的开始温度也要较V-B钢高20℃左右。在含钒、氮低碳贝氏体钢中加入钼、铬将会促进钢的贝氏体相变,但钼的作用要优于铬;钼、铬的加入可使含钒、氮低碳贝氏体钢的贝氏体转变温度降低至少30℃,且贝氏体组织得到了细化,钢的维氏硬度也提高了HV10~30。     

1000MPa级低碳高强钢的组织转变与性能研究

利用膨胀仪测定1 000 MPa级低碳高强钢临界点及CCT曲线,研究不同冷速对试验钢显微组织的影响。结果表明:在0.5～1℃/s冷速范围内,试验钢得到单一粒状贝氏体组织;在2～15℃/s冷速范围内,得到粒状贝氏体、板条贝氏体和马氏体的混合组织;在20～80℃/s的冷却速度范围内,得到板条贝氏体和马氏体的混合组织。以测定CCT曲线为参考依据制定调质工艺,试验钢经过调质后获得优异的综合力学性能。     

B对X100/X120高强度管线钢连续冷却相变组织的影响

 利用热模拟技术（DIL805A热膨胀仪）和显微分析方法,对不同成分体系X100/X120高强度管线钢在连续冷却转变下的显微组织的变化规律进行了研究。研究结果表明,对于无B钢,随冷速增加,组织中依次出现多边形铁素体(PF)、粒状贝氏体(GB)、贝氏体铁素体(BF)和马氏体(M)。B元素的添加使得管线钢相变开始温度降低到500℃左右,抑制了多边形铁素体的形成,促进了贝氏体的形成。为了获得高级别管线钢X100的复相组织,无B钢的冷却速度应控制在20~30℃/s,而含B钢的冷速只需控制在5~15℃/s,简化了冷却工艺。     

Nb-Ti微碳深冲双相钢的连续冷却转变规律

摘要：通过连续冷却实验研究了Nb Ti微碳深冲双相钢在不同冷却速率下的显微组织变化规律。并结合显微组织、热膨胀曲线以及实验钢的硬度值绘制出实验钢的CCT曲线。结果表明,实验钢的CCT曲线由铁素体、珠光体与贝氏体区组成,其中铁素体和贝氏体的区域较大,覆盖冷却速度范围较广。实验冷却速率下未出现马氏体组织。在05～1℃/s的慢冷速下,组织由铁素体和珠光体组成;当冷速增加至3℃/s时,贝氏体开始出现,珠光体消失。当冷速在5～10℃/s范围内时,获得铁素体+贝氏体双相组织;当冷速大于10℃/s时,铁素体相变消失,此时为纯贝氏体转变。热处理过程中若想获得一定量的马氏体组织,退火温度宜设置在820～900℃双相区较低温度范围,使合金元素充分富集于少量奥氏体中,在随后冷却过程中此奥氏体转变为马氏体组织。     

热轧590MPa级车轮钢的奥氏体相变行为

 利用热力模拟试验技术,研究一种Nb-V-Ti复合微合金化C-Mn钢的奥氏体连续冷却相变行为,为低成本高性能热轧590MPa级车轮钢的控制轧制和控制冷却工艺制定提供必要的理论依据。研究表明：无形变条件下,铁素体转变存在的冷却速率范围为0. 5~5℃/s,珠光体转变存在的冷却速率范围为0. 5~2℃/s;形变条件下,铁素体转变存在的冷却速率范围为0. 5~25℃/s,珠光体转变存在的冷却速率范围为0. 5~10℃/s;不论是否存在形变,贝氏体转变存在于整个冷却速率范围(0. 5~30℃/s);奥氏体区形变增加了奥氏体内部的缺陷密度,促进了非均匀形核的发生,故形变促进了铁素体转变;由于试验钢的碳的质量分数较低(＜0. 10%),形变通过促进铁素体相变而间接促进珠光体相变;当贝氏体相变前无铁素体相变时,形变对贝氏体相变有促进作用;试验钢在实际热轧试验中冷却速率宜控制在20℃/s左右,卷取温度控制在550~650℃。     

奥氏体形变对50CrV4钢相变行为的影响

利用Thermecmastor-Z型热模拟试验机,结合金相显微镜(OM)、扫描电镜(SEM)、维氏硬度计等,系统研究了奥氏体区变形对50CrV4钢连续冷却相变和等温相变规律的影响。建立了试验钢动态CCT曲线。研究结果表明,奥氏体变形能促进连续冷却转变过程中铁素体-珠光体、贝氏体转变,但亦可提高奥氏体的机械稳定性,进而抑制马氏体转变,Ms点由331.6℃(奥氏体未变形)降低至291℃(950℃下变形50%+890℃下变形50%,变形速率均为5s-1,变形后冷速为20℃/s)。当轧后冷速小于0.5℃/s时,试验钢中可获得铁素体+珠光体组织。此外,在研究不同变形量对试验钢等温相变规律影响时发现,650℃等温时,试验钢中发生铁素体-珠光体相变。随着变形量的增加(由30%增加至50%),其等温相变动力学加快(相变完成时间由197.6s减小至136.5s),铁素体体晶粒尺寸、珠光体片层间距减小,硬度增加。     

Transformation Behavior of Low Carbon Steels Containing Two Different Si Contents

 Continuous cooling transformation behaviors of low carbon steels with two Si contents (050% and 135%) were investigated under undeformed and deformed conditions. Effects of Si contents, deformation, and cooling rates on γ transformation start temperature (Ar3), phase microstructures, and hardness were studied. The results show that, in the case of the deformation with the true strain of 04, the length of bainitic ferrite laths is significantly decreased in low Si steel, whereas, the M/A constituent becomes more uniform in high Si steel. An increase in cooling rates lowers the Ar3 greatly. The steel with higher level of Si exhibits higher Ar3, and higher hardness both under undeformed and deformed conditions compared with the steel with a lower Si content. Especially, the influence of Si on Ar3 is dependent on deformation. Such effects are more significant under the undeformed condition. The hardness of both steels increases with the increase of cooling rates, whereas, the deformation involved in both steels reduces the hardness.     

Effect of composition and austenite deformation on the transformation characteristics of low-carbon and ultralow-carbon microalloyed steels

Deformation dilatometry has been used to simulate controlled hot rolling followed by controlled cooling of a group of low- and ultralow-carbon microalloyed steels containing additions of boron and/or molybdenum to enhance hardenability. Each alloy was subjected to simulated recrystallization and nonrecrystallization rolling schedules, followed by controlled cooling at rates from 0.1 °C/s to about 100 °C/s, and the corresponding continuous-cooling-transformation (CCT) diagrams were constructed. The resultant microstructures ranged from polygonal ferrite (PF) for combinations of slow cooling rates and low alloying element contents, through to bainitic ferrite accompanied by martensite for fast cooling rates and high concentrations of alloying elements. Combined additions of boron and molybdenum were found to be most effective in increasing steel hardenability, while boron was significantly more effective than molybdenum as a single addition, especially at the ultralow carbon content. Severe plastic deformation of the parent austenite (>0.45) markedly enhanced PF formation in those steels in which this microstructural constituent was formed, indicating a significant effective decrease in their hardenability. In contrast, in those steels in which only nonequilibrium ferrite microstructures were formed, the decreases in hardenability were relatively small, reflecting the lack of sensitivity to strain in the austenite of those microstructural constituents forming in the absence of PF.     

Al对热挤压模具钢 SDAH13连续冷却转变规律的影响

采用热膨胀仪测定Al质量分数分别为0.77%和1.43%以及无Al的热挤压模具钢SDAH13的连续冷却转变曲线,并结合光学显微镜、扫描电镜及显微硬度仪分析Al元素对SDAH13钢相变点、连续转变规律、组织以及硬度的影响.结果表明:Al元素显著提高SDAH13钢的Ac₁、Ac₃和Ms点,降低淬火残留奥氏体含量,同时扩大铁素体及奥氏体两相区.在1060℃奥氏体化温度下,Al元素对SDAH13钢贝氏体相变的临界冷速（0.30℃·s-1）无明显影响,但使贝氏体相区变宽,Al质量分数分别为0.77%和1.43%的SDAH13钢的珠光体相变的临界冷速（0.05℃·s-1和0.3℃·s-1）均高于无Al的SDAH13钢的临界冷速（0.02℃·s-1）,且Al质量分数为1.43%的SDAH13钢在0.02—0.08℃·s-1冷速下出现先共析铁素体组织.Al的加入还使SDAH13钢淬火硬度有所降低.      

Hot Deformation Behavior of V-Microalloyed Steel

Through the expansion curve of continuous cooling transformation at different cooling rates measured by THERMECMASTOR-Z thermal simulator for U75V rail steel,the continuous cooling transformation curve was obtained.The influence on steel microstructure and hardness at different cooling rates was studied.The softening behavior of isothermal deforming in austenite area of 850-1000 ℃ in the interval of passes was also studied by double-pass compression test.The results show that the product of austenite transformation is pearlite when the cooling rate is lower than 10 ℃.When the cooling rate was in the range of 10-50 ℃·s-1,only martensite was received.The hardness of the test steel increases with increasing the cooling rate.Under the condition of deformation of 30% and deformation rate of 3 s-1,the relaxation time for complete recrystallization was shorter than 100 s when deformation temperature was higher than 1000 ℃.When deformation temperature was lower than 880 ℃,complete recrystallization of steel was difficult to achieve even if the relaxation time is extended.     

Computer Model of Phase Transformation From Hot-Deformed Austenite in Niobium Microalloyed Steels

Based on thermodynamics and kinetics, a new mathematical model was developed to calculate the CCT diagrams and the transformation kinetics in low carbon niobium steels, in which the effect of deformation on the degree of supercooling was taken into account. The undercooling caused by deformation is the major reason for the increase of the starting transition temperature during continuous cooling. The critical cooling rate of bainite formation is within 2--5 ℃s for the studied niobium steels and deformation is suitable for the occurrence of pearlite. The ferrite volume fraction increases with the increase of the austenite boundary area, and decreases with the increase of the cooling rate. The calculated CCT diagrams and the volume fraction of each phase are in good agreement with the measurements.     

残留奥氏体对微纳贝氏体钢塑韧性的影响

采用高碳和中碳低温贝氏体转变工艺（095C钢为200℃等温10d,030C钢为320℃等温1d）研究了残留奥氏体对微纳结构钢塑韧性的影响,对不同试样的显微组织、各相体积分数、伸长率和冲击韧性进行观察、检测和分析。试验结果表明,中碳钢贝氏体转变的塑韧性明显高于高碳钢贝氏体转变,主要原因是中碳钢贝氏体转变中存在一定的亚微米级薄膜状残留奥氏体,在拉伸或冲击过程中引起的残留奥氏体的塑性变形,使断裂的能量增加,可以显著提高样品的塑韧性。     

Influence of Mn Content and Hot Deformation on Transformation Behavior of C-Mn Steels

The hot deformation behaviors and the microstructural evolution of plain C-Mn steels with similar contents of C and Si but different contents of Mn have been investigated by compressive processing using Gleeble-1500 mechanical simulator.Influence of Mn and hot deformation on continuous cooling transformation of steels has been studied.The experimental results showed that deformation in austenite region accelerated transformation process,and the extent is dependent on the hot deformation and cooling conditions.The hot deformation would promote transformation process,but the increase of transformation temperature is dependent on Mn contents.The results have also shown that the effect of deformation on ferrite transformation becomes more obvious with the increase of Mn content at relatively low cooling rate.