新一代自润滑无铅易切削钢的开发

 应用炼钢过程中夹杂物控制的热力学模型预测钢包精炼和钢液凝固后钢中氧化物夹杂的成分,在模型预测指导下进行了自润滑易切削钢工业生产试验,并对开发的易切削钢进行了切削性能测试。结果表明,钢中氧化物夹杂预测结果与实测结果一致;用无涂层P10刀具进行的切削试验结果也表明,与传统含铅易切削钢相比,自润滑易切削钢在高速(v≥200 m/min)切削条件下,后刀面磨损降低200%;切削速度v=100 m/min时,二者相当;v=200 m/min时,前刀面月牙洼磨损降低200%,且月牙洼离刀刃较远。说明在高速切削条件下,开发的新一代自润滑易切削钢的切削性能明显优于传统含铅易切削钢,完全可替代传统含铅易切削钢。     

硫化物改质对20MnCr5齿轮钢夹杂物和切削性能的影响

 齿轮钢广泛应用于汽车、机械等传动系统,易切削化是提高齿轮加工效率、降低制造成本的主要途径之一。提高钢中硫元素含量是改善齿轮钢切削性能的有效方式,然而过多的硫元素在轧制时会形成条带状MnS,增大钢的各向异性,因此需要对硫化物进行改制处理。分别采用Ca处理和Mg处理两种方式对20MnCr5齿轮钢进行硫化物改质,通过对力学性能、组织形态、夹杂物分布以及切削性能等表征,对比分析不同改制方式对材料的影响。结果表明,Ca处理和Mg处理后试验钢的强度和塑性保持一致,而Mg处理试样的晶粒尺寸较小,因而韧性较高。Ca处理试验钢中MnS夹杂物数量较多,长条状夹杂物比例相对较高;而采用Mg处理可以有效降低钢中夹杂物的数量,夹杂物平均尺寸有所增大,同时小长径比夹杂物数量增多,但是复合氧化物型夹杂物的数量也有所增加。在240~280 m/min条件下进行了干切削试验,结果表明两种试验钢均出现前刀面磨损、后刀面磨损和边界磨损,其中Ca处理试样的刀具磨损较为严重,同时在较高切削速度下出现了积屑瘤和崩角现象,而Mg处理试样则具有更长的刀具使用寿命,对切削速度的敏感性也较低。分析可知,Mg处理后钢中存在较多的大尺寸球状硫化物夹杂物,提高了应力集中效应,更有利于改善切削性能,因而改制效果更好。     

非金属夹杂物对钙系与钙硫系易切削钢切削性能的影响

研究了在18t钢包中采用喷粉方法生产的钙系与钙硫系易切削钢中非金属夹杂物对切削性能的影响。试验结果表明：以200m/min的速度切削Y40CrCa钢时，刀具寿命比切削40Cr钢时高6－10倍；以160m/min的速度切削Y40CrCaS钢时，刀具寿命比切削40Cr钢时高20倍。经能谱仪查明在刀具后面形成保护薄膜，它是延长刀具寿命的主要原因。     

组织形态对718塑料模具钢切削性能的影响

通过热处理制备出具有回火马氏体组织、下贝氏体组织以及粒状贝氏体组织的718钢,利用光学显微镜、扫描电子显微镜、X射线衍射仪、万能拉伸实验机比较其显微组织及力学性能。同时借助高速铣削实验及光学轮廓仪,研究力学性能以及组织结构对切削性能的影响。结果表明,当切削速度低于145 m·min?1时,贝氏体组织类型比回火马氏体组织更易切削,切削贝氏体组织比切削回火马氏体组织的刀具使用寿命高30%～40%。当切削速度高于165 m·min?1时,马氏体组织发生了加工软化现象,刀具使用寿命提高,切削性能上升。粒状贝氏体组织加工表面因为严重的刀具黏附而出现背脊纹路,马氏体组织具有最佳的切削表面粗糙度。综合考虑之下,三种组织的综合切削性能从高到低排序为:下贝氏体组织、马氏体组织、粒状贝氏体组织,采用300 ℃等温淬火工艺可以有效提升718塑料模具钢的综合切削性能。      

提高钙易切削钢的切削性能

影响易切削钢的切削性能的关键因素是钢中夹杂物。作者采用钢包喷粉的加钙方法,经过实验室规模和工业生产规模的试验,建立了合理的炼钢工艺及喷粉工艺,有效地控制了钢中的夹杂物,从而研制成了切削性能优越的钙易切削钢和钙硫易切削钢。所研制成功的钙易切削钢,具有一项独特的优点,即它的切削刀具寿命竞随切削速度的增加而增加;而钙硫易切削钢,其切削性能比钙易切削钢更高,除刀具寿命长达800min外,切削力也降低了约7％,即电能消耗可降低约7％,这一点在能源紧张的今天也具有非常重要的意义。     

Ti8LC钛合金材料切削过程的有限元仿真及性能试验

钛合金材料的各种特点决定了其难切削的加工性能,针对一种低成本钛合金Ti8LC材料进行了切削加工性能的试验研究.运用有限元法,再现了钛合金切削加工过程,得出了切削参数对主切削力及进给抗力的影响规律,结果表明,随着切削深度的增加,主切削力和进给抗力均有大幅增长,而进给量对切削力的影响不大.而通过进一步的切削加工试验,分析了不同切削速度、进给速度、进给量等工艺参数对钛合金切削加工时的主切削力、进给抗力等的影响,结果表明,由于实际切削中的刀具磨损问题,切削力较仿真切削力大许多.因此,采用目前的涂层硬质合金刀具,该钛合金材料的切削速度应在( 120～160) m·min-1,否则将引起剧烈的刀具磨损而使切削力陡然增加.     

钻头用含硫XGML40Cr钢的开发及其切削性能的改善

邢钢开发的0.020%~0.060%S钻头用XGMI40Cr钢(/%:0.38~0.44C,0.17~0.30Si,0.60~0.80Mn,≤0.035P,0.020~0.060S,0.90~1.10Cr,≤0.01A1)的生产流程为50 t BOF-LF-285 mm×320 mm坯连铸-热轧成Φ12 mm线材。对0.027%S的XGML40Cr和0.006%S的ML40Cr盘条试样进行进刀量0.015 mm/r,切削深度0.1 mm,切削速度12~30 m/min的切削试验。试验结果表明,XGML40Cr断屑性能优于ML40Cr,其切削长度为ML40Cr钢1/5~3/5,XGML40Cr切削过程产生更低的切削热,蓝色切屑比例为10%,ML40Cr钢为70%,XGML40Cr切屑变形系数低于ML40Cr,XGML40Cr表面粗糙度(Ra 10.2μm)优于ML40Cr(Ra 22.4μm)。含硫XGML40Cr钢的力学性能与ML40Cr相当,870℃淬火和500℃回火后的力学性能为抗拉强度1 082 MPa,断面收缩率70%,HRC硬度值40,冲击功A_(KV2)72 J。     

氧含量对硫系易切削钢切削性能的影响

研究了氧含量对硫系易切削钢中硫化物夹杂及对切削性能的影响。结果表明：在一定范围内,钢中氧含量越高越有利于改善切削性能,其原因是氧含量高时,钢中会形成大量的纺锤形（Mn、Fe）（S、O）复合夹杂物。在切削过程中,这类硫化物能割断基体的连续性,在刀具表面形成一层保护膜,从而降低刀具的磨损。实验室切削试验表明：w（O）=0．014％时,硫系易切削钢的切削性能优于45钢,能够获得理想的切削性能。     

20CrMnTiH1齿轮钢中CaS夹杂的形成与控制

利用Factsage软件,对20CrMnTiH1齿轮钢中(CaO)m(Al2O3)n与CaS夹杂形成进行了热力学分析.结果表明:当钢中w(Al)s=0.035％时,要使钢中夹杂物完全转变为液态(CaO)12(Al2O3)7,应控制钢中w(S)低于0.006 7％,w(Ca) /w(Al)高于0.12;本钢液成分条件下,在炼钢温度下不会自发生成CaS夹杂,当钢液温度下降到1 739.8 K时,凝固前沿的w(S)达到0.015 9％,此时会与低熔点(CaO)12(Al2O3)7夹杂表面的CaO反应析出CaS夹杂.通过对某钢厂生产的20CrMnTiH1齿轮钢铸坯中夹杂物的检验发现,实际情况与热力学计算相符合.同时,通过硫偏析方程计算得到:20CrMnTiH1齿轮钢在凝固过程中不析出CaS夹杂的条件为将硫的初始质量分数控制在0.000 318％以下.     

低碳高硫易切削钢中氧化物夹杂对可切削性能的影响

 对现场和实验室冶炼的8炉低碳高硫易切削钢进行切削试验,同时对钢中的非金属夹杂物进行评级和SEM及DES能谱分析。结果表明：无论钢中是否含有锡等易切削元素,低碳高硫易切削钢的刀具磨损量均随钢中B+C类氧化物夹杂级别的增高而明显增加;钢中存在的氧化物夹杂主要为硬质Al2O3-MnO和MnO-SiO2、2MnO-SiO2型氧化物,可加剧切削过程的刀具磨损。钢中氧含量和氧化物夹杂级别相对较低时,适当提高氧含量可促使有利形态的MnS生成而使可切削性能得到改善;当氧含量高时,钢中氧化物夹杂级别明显提高,从而导致可切削性能的明显恶化。     

Application of Thermodynamic Model for Inclusion Control in Steelmaking to Improve the Machinability of Low Carbon Free Cutting Steels

Oxide inclusions formed during steelmaking processes influence the machinability of steel products. At moderate and high cutting speeds, the tool life is dominated by chemical wear. However this wear can be suppressed by engineering exogenous and indigenous glassy oxide inclusions in steel. The present work demonstrates a method to engineer glassy oxide inclusions in a low carbon free cutting steel applying a new thermodynamic model for deoxidation control of steel based on slag‐melt as well as melt‐oxide inclusion equilibration. The model is used online in an industrial production line for the controlled production of glassy inclusions. These inclusions are shown to improve machinability by lubricating the tool‐chip interface during machining of the steel at high cutting speeds. Using an inclusion engineered work piece, the crater wear of an uncoated P10 tool is significantly improved and the tool life is tripled at cutting speeds in the range between 200 and 400 m/min. The industrial results show that thermodynamic modelling is a powerful tool to produce free cutting steels with consistently good machinability behaviour.     

Active wear and failure mechanisms of TiN-Coated high speed steel and tin-coated cemented carbide tools when machining powder metallurgically made stainless steels

In this study, active wear and failure mechanisms of both TiN-coated high speed steel and TiN-coated cemented carbide tools when machining stainless steels made by powder metallurgy in low and high cutting speed ranges, respectively, have been investigated. Abrasive wear mechanisms, fatigue-induced failure, and adhesive and diffusion wear mechanisms mainly affected the tool life of TiN-coated high speed steel tools at cutting speeds below 35 m/min, between 35 and 45 m/min, and over 45 m/min, respectively. Additionally, fatigue-induced failure was active at cutting speeds over 45 m/min in the low cutting speed range when machining powder metallurgically made duplex stainless steel 2205 and austenitic stainless steel 316L. In the high cutting speed range, from 100 to 250 m/min, fatigue-induced failure together with diffusion wear mechanism, affected the tool life of TiN-coated cemented carbide tools when machining both 316L and 2205 stainless steels. It was noticed that the tool life of TiN-coated high speed steel tools used in the low cutting speed range when machining 2205 steel was longer than that when machining 316L steel, whereas the tool life of TiN-coated cemented carbide tools used in the high cutting speed range when machining 316L steel was longer than that when machining 2205 steel. formerly with the Laboratory of Engineering Materials, Helsinki University of Technology     

Design of steels for high speed machining

Abstract

Historical analysis of metal cutting shows that metal removal rates have been increasing in the course of the century, predicated by the advancement in tool materials but the steel design has lagged behind. This paper examines the mechanisms of chip formation and tool wear as a function of cutting speed in metal cutting. Chemical wear is identified as the dominant mechanism of tool wear at high cutting speeds caused by temperature rise due to shear localisation in the primary and secondary shear zones of chip. Shear localisation in the primary shear zone is shown to be influenced by both microstructural parameters, i.e. matrix hardening and second phase particles, and metal cutting variables, i.e. cutting speed (strain rate) and feed (pressure). Shear localisation in the secondary shear zone is caused by the tribological conditions of seizure at the tool/chip interface. Chemical crater wear is caused by the dissolution of tool into the workpiece (chip) by diffusion mechanism and can be prevented by suppressing the tribological condition of seizure. The design of steel for high speed machining is based on engineering glassy oxide inclusions in steel, which are designed to form a viscous layer in situ at the tool/chip interface at high cutting speeds. The viscous layer lubricates the tool/chip interface and prevents the occurrence of seizure, thereby suppressing chemical crater wear. In comparison with the large volume fraction of inclusions required for promoting ductile fracture at low cutting speeds, the amount of inclusions required for lubricating the tool/chip interface is very small and is in the range that is typical of clean steel. Thermodynamic modelling is shown to be a powerful tool to engineer glassy oxide inclusions in steel     

20CrMnTiH齿轮钢0120 mm棒材硬点缺陷分析及改善措施

通过金相显微镜、扫描电镜和能谱仪分析了20CrMnTiH齿轮钢Φ120 mm棒材锯切下料过程硬点缺陷成因。结果表明,齿轮钢棒材试样内部存在30～80μm大颗粒夹杂物聚集是造成齿轮钢锯切过程硬点缺陷的主要原因。这些大颗粒夹杂物主要为Al₂O₃夹杂物和TiN夹杂物的聚集。通过控制120 t转炉出钢钢水溶解氧含量小于200×10^-6、调整精炼终点钙铝参数（0.015%～0.025%Al,0.0015%～0.0020%Ca）、连铸保护浇铸减少过程吸氮、浇铸钢水温度由1530℃降至1525℃、优化二冷配水加速钢的凝固等措施,消除了转炉生产20CrMnTiH齿轮钢硬点缺陷。     

高拉速连铸低碳铝镇静钢铸坯中夹杂物

针对高拉速板坯连铸生产的低碳铝镇静钢铸坯,采用Aspex自动扫描电镜对铸坯表层夹杂物进行大面积的扫描分析,得到不同拉速下夹杂物的变化规律,并探究流场和S含量对夹杂物分布的影响.结果表明:随着拉速增大,钩状坯壳的深度和长度逐渐减小.对拉速大于2 m·min-1的铸坯,由于钩状坯壳不是很发达,铸坯表层没有发现大于200μm的夹杂物.铸坯表层尺寸介于50~200μm的夹杂物主要是由凝固坯壳所捕获,而夹杂物在凝固前沿的受力决定了夹杂物的捕获行为.随着拉速提高,凝固前沿的钢液流速增加,随着冲刷力的增加、捕获力的减少,夹杂物被捕获的数量减少.在高拉速连铸下,如果钢液中S含量较大,夹杂物受到明显的温度Marangoni力,会更容易被凝固坯壳捕获.      

不同相组成的硅黄铜组织性能的研究

通过OM、XRD以及TG/DTA等测试技术,系统研究了(α+β)双相、单一β相以及(β+γ)双相无铅硅黄铜的组织结构、硬度、铣削性能以及脱锌腐蚀等性能.结果表明:(α+β)硅黄铜虽然铣削力较低,但切屑形态欠佳,且平均脱层厚度大,为438.12μm;而(β+γ)相硅黄铜不仅切屑形态最差,硬度最高,达273.7 HB,因而铣削力也最大,增加刀具的磨损,降低刀具寿命;β相硅黄铜虽然铣削力稍高,但切屑形态为细小卷筒状,呈最优切屑形态,且在抗脱锌腐蚀测试中,β相硅黄铜平均脱锌层厚度最小,为262.94μm,所以β相硅黄铜综合性能最佳,(β+γ)硅黄铜不适合做切削黄铜,而(α+β)硅黄铜的切削性能和耐腐蚀性能都有待改进.     

优化脱氧工艺提高38CrMoAl钢连浇成功率

研究了连铸38CrMoAl钢(/％:0.35 ～ 0.42C、0.20 ～ 0.45Si、0.30 ～0.60Mn、1.35 ～ 1.65Cr、0.15～0.25Mo、0.70 ～ 1.10Al)夹杂物类型和形成原因.通过优化脱氧制度:提高60 t EAF终点[C] ≥0.010％,保持高碱度渣(R≥2.5),出钢前2 ～3 min向熔池喷吹碳粉,控制(FeO),出钢过程减少Si-Fe加入量;LF喂铝线并用铝粒扩散脱氧,采用(/％)50～60CaO、10 ～ 15SiO2、15 ～ 20Al2O3、≤0.7(FeO+ MnO)、≤5MgO高碱度渣;做好VD后保护浇铸,有效地降低钢中Al2O3类型非金属夹杂物.结果表明,优化工艺后38CrMoAl钢连浇炉数达到9炉,夹杂物废品率≤1％.     

非真空吹氮工艺对316L奥氏体不锈钢吸氮行为的影响

在实验室通过刚玉坩埚-硅钼棒电阻炉研究了吹氮时间(0～50 min),氮气分压(35～100kPa),吹氮流量(总流量0.3 L/min;N₂:Ar=1:3～3:1),钢液温度(1 773～1 833 K)对0.8 kg 316 L不锈钢液(%:0.031C、16.13Cr、10.12Ni、2.12Mo)中氮含量的影响。结果表明,钢中氮含量随着吹氮时间、氮分压的增加而增大,随吹氮流量增加钢液氮含量达到饱和的时间缩短,氮的溶解度随着钢液温度的降低而升高。应用热力学模型和动力学模型对实验结果进行分析。