Development of non-quenched and tempered bolt steel

The 8.8 grade non-quenched and tempered bolt steel was studied according to the process conditions of wire rod plant and customer requirments.Three types of experimental steel grades were selected.10MnSiTi Nb and 20Mn2VTi(N) were chosen as the formal steel after several experimemts.

Effect of inclusions on the formation of acicular ferrite in Ti-bearing non quenched-and-tempered steel

Nucleation of acicular ferrite and its influence factors in non quenched-and-tempered steel was studied by using TEM and thermodynamic calculation. The results show that the complex particles with a center made of Ti oxide, Al2O3, and silicate and an outside made of a small quantity of mixture of TiN and MnS are able to act as ferrite nucleation nuclei. The acicular ferrite percentage changes little with Ti. When the oxygen content was 80 ppm, the volume percentage of acicular ferrite decreased due to an increase in allotriomorphic ferrite. The larger the cooling rate and the shorter the incubation time, the finer the titanium oxide and the higher the nucleation ratio of acicular ferrite.

Theoretical calculation of the impact work in the alloying non-quenched and tempered steel

Coupled with hot-continuous rolling technology and based on the calculation of the finishing rolling impact work in the non-quenched and tempered Si-Mn steel, the calculations of the finishing rolling impact work in the alloying non-quenched and tempered steel with the elements of Cr, Ni, Mo, W, Cu, V, Nb and Ti are studied with the covalent electron number nA of the strongest bond in alloying phases, the smallest electron density difference ?ρ of phase interfaces, and the number of atom states σ (σ′) which keep the interface electron density continuous. The calculated results show that the finishing rolling impact work of the alloying non-quenched and tempered steel intensely depends on strengthening mechanisms. The solution strengthening, interface strengthening, precipita- tion strengthening of pearlite, and dispersion strengthening will result in the decrease of the finishing rolling impact work; the refinement strengthening, the precipitation strength- ening of V, Nb and Ti in α-Fe-C-V(Nb, Ti), and the residual austenite containing Ni on the boundary of α-Fe-C-Ni will increase the impact work; and the increments or decrements can be calculated with nA, ?ρ, σ (σ′) and weights of alloying elements. The calculation formulas of the finishing rolling impact work in this paper are intergraded with the sug- gested ones of the finishing rolling tensile strength, yield strength, and elongation of the non-quenched and tempered steel. The calculated results agree well with the measured ones.

Theoretical calculation of the finishing rolling impact work in non-quenched and tempered Si-Mn steel

Based on the hot-continuous rolling technology, the finishing rolling impact work α k of the non-quenched and tempered Si-Mn steel is theoretically calculated with the covalent electron number nA of the strongest bond in alloying phases, and the smallest interface electron density difference Δρ of alloying phase interface and the number of atom states σ which keep the interface electron density continuous. Calculations show that the solution strengthening, the precipitation strengthening, and the interface strengthening will result in the decrease of the finishing rolling impact work α k, and the effects of the number of atom states σ which keep the interface electron density continuous on the finishing rolling impact work α k are different. Taking the impact work and the number of atom states σ 0 keeping the electron density continuous of the phase interface α-Fe/α-Fe-C between α-Fe and α-Fe-C as reference values, the impact work of the interface will increase when σ of some interface is larger than σ 0; otherwise, the impact will decrease. Therefore, the finishing rolling impact work α k can be calculated with the impact value of the refined α-Fe matrix and the influence amounts caused by the solution strengthening, the precipitation strengthening, the interface strengthening, and the number of atom states σ which keep the interface electron density continuous. The calculated results agree well with the measured ones. In this paper, the effect of S on the impact work is also discussed.

In situ observation and thermodynamic calculation of MnS in 49MnVS3 non-quenched and tempered steel

Based on thermodynamics calculation, the results of the formation temperature of MnS inclusions of non-quenched and tempered steel during heating process were dis- cussed. It is shown that while the solid fraction is 0.9, MnS inclusions began to precipitate in the final stage of solidification. The solidification process of 49MnVS3 non-quenched and tempered steel during heating has been observed in situ using a confocal scanning laser microscope （CSLM）, which agrees well with the thermody- namics calculation. MnS particles were coarsening during heating process, which would reduce the pinning effect on the austenite grain boundaries and bring about the ~11rtden ~r^wth ~f ,qnrn~ ~11,qtenif.~ ~r^ins in thi~ st~.g~.

Effect of Nb-V Microalloying on Microstructures and Mechanical Properties of Medium Carbon Non-Quenched and Tempered Steel

Based on optical microscope(OM),transmission electron microscope(TEM) and mechanical performance measurement,the microstructures and mechanical properties of Nb-V micro-alloying non-quenched and tempered steels have been studied.The results showed that the microstructure consists of ferrite and pearlite,in which there exists a lot of intragranular ferrite.Niobium carbide is the main form of carbonitrides,Nb-enriched carbonitrides refine grains,V-enriched carbonitrides have precipitation strengthening effect,which promotes the toughness of the studied steel.The mechanical properties for steels 1,2 and 3 have met the standards required by high load automobile crankshaft,in which the comprehensive property for No.2 is the best.

Effects of Rare Earths on the Tempering Transformation Kinetics of High Carbon Steel

Effect of rare earth metals (REM) on tempering process and decomposition kinetics of martensite and retained austenite of high carbon steel were investigated by DSC technique,based on the non-isothermal kinetic theory.The result shows that the addition of REM in high carbon steel increases the decomposition temperatures of martensite and retained austenite,decreases the thennal effect values,elevates the activity energies and changes the transformation mechanism.

Fe-3%Si平面流铸带平整轧制退火过程中组织织构演变

采用平面流铸技术制备了Fe-3%Si无取向硅钢极薄带,研究了平面流铸Fe-3%Si薄带平整轧制与退火处理的组织织构演变规律。结果表明,平面流铸带具有大比率的柱状晶组织,{100}取向晶粒占比高于30%,也即存在对磁性能有益的{100}织构。小压下率冷轧平整过程中,晶粒取向变化及晶内取向分裂程度整体不高,形变行为存在取向依赖性。{100}取向晶粒形变储能积累程度相对较低,经退火处理后该组分体现出遗传优势,在退火组织中占比仍超过30%。退火组织中小尺寸晶粒有所增加,且绝大部分小尺寸晶粒偏离{100}取向,这导致了退火组织平均晶粒尺寸降低,并在一定程度上弱化{100}织构。

38MnVTi非调质钢的TTT曲线的测定与分析

研究了38MnVTi非调质钢在等温冷却过程中的奥氏体转变产物及转变量与时间的关系。通过Gleeble-1 500D热模拟试验机获得不同等温温度的膨胀曲线。采用膨胀法,通过Gleeble-1 500D热模拟试验机获得不同等温温度的膨胀曲线,再计算和运用Origin软件拟合得到38MnVTi非调质钢的等温转变曲线(TTT曲线)。结果表明:38MnVTi非调质钢渗碳体的析出温度为750℃、铁素体析出温度为840℃、马氏体析出温度为360℃以及马氏体转变终止温度为212℃。在540、510、480、430℃等温冷却条件下贝氏体的最大转变量分别为16.9%、26.8%、38.5%、55.3%。

35CrMo钢蓄能器开裂原因

某公司生产的蓄能器在使用1 a后发生开裂现象。采用宏观观察、化学成分分析、力学性能测试、扫描电镜分析、金相检验等方法对蓄能器的开裂原因进行分析。结果表明:制做蓄能器壳体的35CrMo钢存在微裂纹;蓄能器工作时,内部介质气体和液压油产生的压力使微裂纹逐步扩展并贯穿管壁,导致蓄能器开裂。

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。

8.8级非调紧固件用10B21盘条研究与开发

采用转炉→精炼炉→真空脱气→方坯连铸→加热→粗轧→中轧→精轧→减定径→吐丝→XDWP(Xingcheng Direct Water Patenting)冷却→斯太尔摩风冷冷却的方式试验生产基于10B21钢的8.8级非调紧固件用热轧盘条。通过控制减定径温度为813℃,吐丝温度为828℃,斯太尔摩辊道速率设置为0.75 m/s,在连续经过XDWP冷却和斯太尔摩风冷后获得的热轧盘条抗拉强度达到680 MPa,断后伸长率为23.6%,断面收缩率为75%,力学性能完全满足GB/T 29087―2012的要求。且经过1/4冷顶锻和25%的大减面率拉拔试验,其结果满足紧固件用户使用要求。

活塞杆电镀后表面缺陷原因分析

针对非调钢活塞杆电镀后表面缺陷,通过宏观、金相、扫描电镜等分析,发现表面缺陷为磨削工序中的铁屑经超声碱洗未清除,电镀后与基体结合力不良,在抛光工序中镀层脱落形成的镀层起皮缺陷。在活塞杆电镀前加强表面清洗、表面检查,对表面存在的氧化皮、粘附异物进行清理和去除,可有效减少活塞杆表面镀层起皮缺陷。

易切削非调质汽车用钢表面裂纹形成机理及工艺优化

易切削非调质汽车用钢采用410 mm×530 mm大断面连铸坯轧制成规格Φ130~220 mm的钢材,表面探伤合格率较低,钢材表面出现裂纹缺陷,通过对钢轧全流程系统分析发现为连铸坯表面角部横裂纹和星状裂纹所导致,其与结晶器铜管倒锥度及R角不合理、钢中硫化物形态及偏析聚集、保护渣理化指标适配性差、二次冷却系统工艺有待优化等方面原因有关。通过改进结晶器铜管倒锥度及R角、微钙化处理工艺改善钢中硫化物形态、调整结晶器保护渣的理化性能指标、优化二次冷却系统,酸洗试样表面质量合格率提高了近30%,铸坯表面磁粉探伤合格率提高至99.2%,连铸坯所对应轧材的表面探伤最高炉次达98.6%、最低炉次达92.4%,铸坯纵剖酸洗试样V型偏析改善明显,且碳、硫的中心偏析指数分别为1.04、0.97,符合±0.05的高标准均质化要求。

非调质钢1E1106“黑心”问题研究

对不同规格不同程度出现“黑心”超标试样进行低倍、成分偏析、晶粒度和金相组织分析,结果显示,由于成分C、Mn偏聚在钢坯中心,造成心部大颗粒珠光体产生,表明成分偏析是导致非调质钢1E1106冷蚀“黑心”的主要原因。

汽车曲轴用非调质钢C38+N的热变形行为研究

以重型汽车曲轴用C38+N非调质钢为对象,对其热变形行为开展实验研究。对C38+N钢在850~1250℃保温不同时间时的奥氏体晶粒长大行为进行研究。得出模铸轧材和连铸轧材C38+N钢奥氏体晶粒长大激活能分别为7.49×10^(4)J/mol、7.87×10^(4)J/mol。计算并建立了不同实验状态下的奥氏体晶粒长大模型,分析了C38+N钢模铸轧材、连铸轧材奥氏体晶粒长大行为差异的原因是连铸轧材比模铸轧材的MnS分布更加弥散,MnS对奥氏体晶界有钉扎作用。

轧后控制冷却对非调质钢F45MnVS组织和性能的影响

对非调质钢F45MnVS进行轧后控制冷却试验,对比了轧后未冷却与控制冷却的钢材热轧态力学性能、脱碳层和显微组织。结果表明,轧后控制冷却对钢材下屈服强度、延伸率、断面收缩率和常温冲击功均有明显改善作用;钢材表面脱碳层在轧后控制冷却条件下可以得到有效控制,甚至脱碳层“消失”;在钢材轧后表面温度冷却至650℃时,表层区域出现少量粒状贝氏体,而在钢材轧后表面温度冷却至460℃时,表层区域出现大量粒状贝氏体。轧后控制冷却使钢材表层区域和1/2半径附近的铁素体和珠光体组织被细化,铁素体网状比例降低,长条铁素体转变为块状铁素体;因钢材尺寸较大,心部区域显微组织差异性较小。

V(C,N)在V-N微合金非调质钢奥氏体中的析出动力学

在Gleeble-3500热模拟试验机上采用应力松弛法,研究了38MnSiVS非调质钢在750~950℃、10%~40%变形量条件下的析出-时间-温度(precipitation-time-temperature,PTT)曲线。基于Dutta和Sellars提出的应变诱导析出模型(DS模型),建立了等温析出动力学模型,计算得到理论PTT曲线。通过与试验PTT曲线比较,得出模型对钢的析出鼻尖温度、析出开始时间和结束时间的预测较为精准。采用“时间补偿法”建立了连续冷却析出动力学模型,计算出连续冷却过程析出相的体积分数和平均尺寸,与透射电子显微镜和能谱分析结果基本一致,而且冷速的增大可抑制钒的析出,细化析出相,表明模型可以准确地预测钒微合金非调质钢的连续冷却析出过程。最后,通过析出强化增量计算得出,V(C,N)析出强化对38MnSiVS非调质钢强度的贡献较大。

胀断连杆用中碳非调质KNF33MAM钢的成分与组织

用非调质钢材料代替调质钢材料来制造发动机胀断连杆,可以省去一道热处理工序,从而利于节能环保,采用胀断技术代替传统的平切技术,有利于提高连杆的装配精度。对胀断连杆用KNF33MAM非调质钢的化学成分、低倍组织、显微组织、非金属夹杂物等方面进行分析,结果可为提高国内材料水平奠定理论基础。

35MnVS非调质钢针状铁素体形核原位观察

非调质钢生产过程中由于省去了淬火、回火等热处理工序,符合倡导的高效节能钢的发展要求。然而,非调质钢产品仍会出现铁素体晶粒粗大等问题,导致组织和性能不均匀,严重影响其使用寿命。本研究利用高温激光共聚焦显微镜,采用样品表面熔化的方法,研究非调质钢中微观组织的演变过程及铁素体形核规律,以及铁素体异质形核的特点。结果表明:非调质试样钢凝固过程相的转变阶段主要分为:1480℃时液相开始向奥氏体转变,1420℃到1400℃为TiN-MnS夹杂物的形核析出温度区间,780℃为α-Fe相的开始形核温度;原位观察实验中,当样品温度下降到1420℃左右时,钢中开始析出尺寸细小的Al 2O 3-MgO夹杂物,而试样冷却至室温时,试验钢中的夹杂物主要成分为TiN-MnS;热力学计算结果表明,在785℃时奥氏体开始向铁素体发生转变,α-Fe含量不断增多,并在690℃时达到最大值,和原位观察实验结果基本一致。本研究对理解氧化物冶金过程,及进一步改进该工艺和应用效果,均具有重要意义。