第44卷 第4期 2009年4月钢铁Iron and SteelVo l.44,N o.4April 2009变形温度与冷却速率对含Nb 中碳钢晶粒细化的影响赵英利1,2, 时 捷2, 董 瀚2, 谢 刚1(1.昆明理工大学材料与冶金工程学院,云南昆明650093; 2.钢铁研究总院结构材料研究所,北京100081)摘 要:利用G leeble 1500热模拟试验机,以含N b 中碳钢为研究对象,研究了不同变形温度与冷却速率对再加热淬火后奥氏体晶粒细化的影响及其晶粒细化的机制。
结果表明:经热变形后直接淬火+再加热淬火工艺得到的奥氏体晶粒尺寸均小于10 m,且随热变形温度的降低,原奥氏体晶粒由等轴晶粒变成扁平化晶粒,经再加热淬火后,得到的奥氏体晶粒逐渐细化;与变形后以5 /s 冷速缓冷的工艺相比,变形后直接淬火经再加热淬火后的奥氏体晶粒细化更明显。
关键词:晶粒细化;再结晶;直接淬火;逆相变中图分类号:T G 142 4 文献标识码:A 文章编号:0449 749X (2009)04 0077 05Effect of Deformation Temperature and Cooling Rate on GrainSize Refining of Medium Carbon Nb Bearing SteelZH AO Ying li 1,2, SH I Jie 2, DONG H an 2, XIE Gang 1(1.School of M ater ial and M etallurg y Engineer ing ,Kunming U niv er sity of Science and T echnolog y,K unming 650093,Yunnan,China; 2.Institute for Structural M ateria ls,Centr al I ron and Steel R esear ch Institute,Beijing 100081,China)Abstract:By using Gleeble 1500machine,the effect of differ ent defo rmatio n temper ature and cooling rate o n gr ain refinement o f austenite g rains after reheat quenching and the mechanism of g rain refinement wer e studied.T he re sults show that austenite g rains size are all less than 10 m by hot defo rm follo wed by direct quenching,and then re heat quenching ,austenite g rains r efining wit h decreasing defo rmation temperature as a r esult of pr io r austenite gr ains become fro m equiax ed g rains to pancake g rains;T he finer austenite g rain can be obtained by hot defo rm fo l low ed by dir ect quenching and then r eheat quenching ,compared w ith hot deform fo llow ed by slow cooling at 5 /s and then r eheat quenching.Key words:g r ain refinement;recr ystallizatio n;direct quenching;rev erse transfor mation作者简介:赵英利(1981 ),男,博士生; E mail :zyl8401292@163 com; 修订日期:2008 07 31钢铁结构材料正在朝 超细晶、高洁净、高均匀!的 新一代钢铁材料!发展,其中核心技术是超细晶,按照H all Perch 关系式,通过将当前工业细晶粒尺寸(一般为20 m 左右)细化一个数量级,钢铁材料的强度可提高一倍,同时保持良好的塑性和韧性配合[1]。
STEEL FORMING AND HEAT TREATING HANDBOOKAntonio Augusto GorniSão Vicente, Brazilwww.gorni.eng.brRelease #12 – 12 April 2005USEFUL METALLURGICAL FORMULAS- Austenite Formation Temperatures. GrangeAe Mn Si Cr Ni 1133325404226=−++−Notation:Ae 1: Equilibrium Temperature for Austenitization Start [°F]Alloy Content : [weight %]Ae C Mn Si Cr Ni 315703232580332=−−+−−Notation:Ae 3: Equilibrium Temperature for End of Austenitization [°F]Alloy Content : [weight %]Source: GRANGE, R.A. Metal Progress , April 1961, 73.Ae Mn Si Cr Ni As W 1723107291169169290638=−++−++,,,,,Notation:Ae 1: Equilibrium Temperature of Austenitization Start [°C]Alloy Content : [weight %]. AndrewsNotation:Ae 3: Equilibrium Temperature for End of Austenitization [°C]Alloy Content : [weight %]Notes:- Both formulas are valid for low alloy steels with less than 0,6%C.Source: ANDREWS, K.W. Empirical Formulae for the Calculation of Some Transformation Temperatures. Journal of theIron and Steel Institute , 203, Part 7, July 1965, 721-727.. RobertsAe Mn Cr Cu Si P Al F n 391025112060700250=−−−++−−Notation:Ae 3: Equilibrium Temperature for End of Austenitization [°C]Alloy Content : [weight %]F n : value defined according to the table below:C F n0,05 240,10 480,15 64 0,20 800,25 930,30 1060,35 1170,40 128Source: ROBERTS, W.L.: Flat Processing of Steel ; Marcel Dekker Inc., New York, 1988.. EldisAe Mn Ni Si Cr Mo 171217819120111998=−−+++,,,,,Notation:Ae 1: Equilibrium Temperature of Austenitization Start [°C]Alloy Content : [weight %]Notation:Ac 3: Equilibrium Temperature for End of Austenitization [°C]Alloy Content : [weight %]Notes:- Both formulas were proposed by ELDIS for low alloy steels with less than 0,6%C.Source: BARRALIS, J. & MAEDER, G. Métallurgie Tome I: Métallurgie Physique. Collection Scientifique ENSAM ,1982, 270 p.- Austenite Transformation Temperatures. BorattoNotation:T nr : Temperatura of No-Recrystallization [°C]Alloy Content : [weight %]Source: BORATTO, F. et al.: In: THERMEC ‘88. Proceedings. Iron and Steel Institute of Japan, Tokyo, 1988, p. 383-390.. OuchiAr C Mn Cu Cr Ni Mo h 391031080201555800358=−−−−−−+−,()Notation:Ar 3: Start Temperature of the Transformation Austenite → Ferrite [°C]Alloy Content : [weight %]h : Plate Thickness [mm]Notes:- This formula was determined using data got from samples cooled directly from hot rolling experiments. Thus it includes the effects of hot forming over austenite decomposition.Source: OUCHI, C. et al.: Transactions of the ISIJ , March 1982, 214-222.. ChoquetAr C Mn Si 39025276260=−−+Notation:Ar 3: Start Temperature of the Transformation Austenite → Ferrite [°C]Alloy Amount : [weight %]Notes:- This formula was determined using data got from samples cooled directly from hot rolling experiments. Thus it includes the effects of hot forming over austenite decomposition.Source: CHOQUET, P. et al.: Mathematical Model for Predictions of Austenite and Ferrite Microstructures in Hot RollingProcesses. IRSID Report , St. Germain-en-Laye, 1985. 7 p.. Nippon Steel 1Ar C Mn Si P 3879451616573802747=−−++,,,,,Notation:Ar 3: Start Temperature of the Transformation Austenite → Ferrite [°C]Alloy Content : [weight %]Ar C Mn 1706435041182=−−,,,Notation:Ar 1: Final Temperature of the Transformation Austenite → Ferrite [°C]Alloy Content : [weight %]Notes:- It is unknown the previous conditioning of the steel samples that supplied data for the deduction of this formula.- Samples cooled at 20°C/s.Source: R&D Team of the Kimitsu Steelworks of Nippon Steel , 2003.. Nippon Steel 2Cr Al P Si Mn C Ar 204028733923259013−+++−−=Notation:Ar 3: Start Temperature of the Transformation Austenite → Ferrite [°C]Alloy Content : [weight %]Notes:- It is unknown the previous conditioning of the steel samples that supplied data for the deduction of this formula.Source: R&D Team of the Kimitsu Steelworks of Nippon Steel , 2003.. StevenB C Mn Cr Ni Mo s =−−−−−152648616212667149B Bs 50108=−B Bs 100216=−Notation:B s : Start Temperature of the Bainitic Transformation [°F]Alloy Amount : [% em peso]B x : Temperature Required for the Formation of x% of Bainite [°F]Source: STEVEN, W. et al. Journal of the Iron and Steel Institute , 183, 1956, 349.. SuehiroB C Mn s =−−718425425.Notation:B s : Start Temperature of the Bainitic Transformation [°F]Alloy Amount : [weight %]Source: SUEHIRO, M. et al. Tetsu-to-Hagané, 73 (1987), p. 1026-1033.. RowlandM C Mn Si Cr Ni Mo W s =−−−−−−−930600602050302020Notation:M s : Start Temperature of the Martensitic Transformation [°F]Alloy Amount : [% em peso]Source: ROWLAND, E.S. et al. Transactions ASM , 37, 1946, 27.. StevenM Ms 1018=−M Ms 5085=−M Ms 90185=−M Ms 100387=−Notation:M x : Temperature Required for the Formation of x% of Martensite [°F]Source: STEVEN, W. et al. Journal of the Iron and Steel Institute , 183, 1956, 349.. AndrewsM C Mn Ni Cr Si Mo s =−−−−−−53942330417712111070,,,,,Notation:M s : Start Temperature of the Martensitic Transformation [°C]Alloy Content : [weight %]Notes:- Formula valid for low alloy steels with less than 0,6%C.Source: ANDREWS, K.W. Empirical Formulae for the Calculation of Some Transformation Temperatures. Journal of theIron and Steel Institute , 203, Part 7, July 1965, 721-727.. EldisM C Mn Ni Cr s =−−−−5313912433218162,,,,Notation:M s : Start Temperature of the Martensitic Transformation [°C]Alloy Content : [weight %]Notes:- Equation developed by Eldis- Equation valid for steels with chemical composition between the following limits: 0.1~0.8% C; 0.35~1.80% Mn; <1.50% Si; <0.90% Mo; <1.50% Cr; <4.50% Ni .Source: BARRALIS, J. & MAEDER, G. Métallurgie Tome I: Métallurgie Physique. Collection Scientifique ENSAM , 1982, 270 p.. KraussM C Mn Cr Ni Mo s =−−−−−56147433171721Notation:M s: Start Temperature of the Martensitic Transformation [°C]Alloy Amount: [% em peso]Source: KRAUSS, G. Principles of Heat Treatment and Processing of Steels, ASM International, 1990, p. 43-87.- Austenitization Time-Temperature Equivalency Parameter. Isothermal AustenitizingNotation:P a: Austenitization Time-Temperature Equivalence Parameter in Terms of Grain Size [K]T a: Austenitization Temperature [K]R: Molar Gas Constant, 8.314 JK-1mol-1t a: Soaking time under T a∆H a: Activation Energy of Austenitic Grain Coarsening, 460 kJmol-1 for low alloy steels. Anisothermal AustenitizingIn this case P a is the period of heating/cooling time between T max and T min, whereT max: maximum temperature during the austenitizing treatment;T min : temperature calculated according to the following equation:Source: BARRALIS, J. & MAEDER, G. Métallurgie Tome I: Métallurgie Physique. Collection Scientifique ENSAM ,1982, 270 p.- Equivalent Carbon – H.A.Z. Hardenability. Dearden & O’Neill (1940)2001200_max −=Dearden EQ C HVNotation:C EQ_Dearden : Equivalent Carbon (Dearden) [%]Alloy Content : [weight %]HV max = Dureza Máxima [Vickers]Source: Y URIOKA, N.: Physical Metallurgy of Steel Weldability . ISIJ International , 41:6, June 2001, 566-570.. IIW - International Institute of WeldingNotation:C EQ_IIW : Equivalent Carbon (IIW) [%]Alloy Content : [weight %]Source: H EISTERKAMP, F. et al.: Metallurgical Concept And Full-Scale Testing of High Toughness, H 2S Resistant0.03%C - 0.10%Nb Steel . C.B.M.M. Report , São Paulo, February 1993.. BastienBastien EQ m C CR _6,109,13)ln(−=Notation:C EQ_Bastien : Equivalent Carbon (Bastien) [%]Alloy Content : [weight %]CR m : Critical Cooling Rate at 700°C [°C/s] (that is, minimum cooling rate that produces a fully martensitic structure)Source: Y URIOKA, N.: Physical Metallurgy of Steel Weldability . ISIJ International , 41:6, June 2001, 566-570.. Yurioka et al.8,46,10)log(_−=Yurioka EQ m C tNotation:C EQ_Yurioka : Equivalent Carbon (Yurioka) [%]Alloy Content : [weight %]t m : Critical Cooling Time from 800 to 500°C [s] (that is, maximum cooling time that produces a fully martensiticstructure)Source: Y URIOKA, N.: Physical Metallurgy of Steel Weldability . ISIJ International , 41:6, June 2001, 566-570.. Kihara et al.Notation:C EQ_Kihara : Equivalent Carbon (Kihara) [%]Alloy Content : [weight %]Source: Y URIOKA, N.: Physical Metallurgy of Steel Weldability . ISIJ International , 41:6, June 2001, 566-570.- Equivalent Carbon – Hydrogen Assisted Cold Cracking. DNVNotation:C EQ_DNV: Equivalent Carbon (DNV) [%]Alloy Content: [weight %]Source: Y URIOKA, N.: Physical Metallurgy of Steel Weldability. ISIJ International, 41:6, June 2001, 566-570. . Uwer & HohneNotation:C EQ_Uwer: Equivalent Carbon (Uwer & Hohne) [%]Alloy Content: [weight %]Source: Y URIOKA, N.: Physical Metallurgy of Steel Weldability. ISIJ International, 41:6, June 2001, 566-570.Mannesmann.Notation:C EQ_PLS: Equivalent Carbon for Pipeline Steels [%]Alloy Content: [weight %]Notes:-Formula deduced for pipeline steels- A version of this formula divides V by 15Source: H EISTERKAMP, F. e outros: Metallurgical Concept And Full-Scale Testing of High Toughness, H2S Resistant0.03%C - 0.10%Nb Steel. C.B.M.M. Report, São Paulo, February 1993.. GravilleNotation:C EQ_HSLA: Equivalent Carbon (Uwer & Graville) [%]Alloy Content: [weight %]Notes:-Formula deduced for pipeline steelsSource: Y URIOKA, N.: Physical Metallurgy of Steel Weldability. ISIJ International, 41:6, June 2001, 566-570.. Bersch & KochNotation:C EQ_Bersh: Equivalent Carbon for Pipeline Steels [%]Alloy Content: [weight %]Notes:- Formula deduced for pipeline steelsSource: P ATCHETT, B.M. et al.: Casti Metals Blue Book: Welding Filler Metals. Casti Publishing Corp., Edmonton, February 1993, 608 p. (CD Edition).. Ito & Bessyo (I)Notation:P cm: Cracking Parameter [%]Alloy Content: [weight %]Notes:- Formula deduced for pipeline steels with C < 0,15%- This is the most popular formula for this kind of material.Source: H EISTERKAMP, F. e outros: Metallurgical Concept And Full-Scale Testing of High Toughness, H2S Resistant0.03%C - 0.10%Nb Steel. C.B.M.M. Report, São Paulo, February 1993.. Ito & Bessyo (II)Notation:P c: Cracking Parameter [%]Alloy Content: [weight %], exceptH: Hydrogen amount in the weld metal, [cm³/100 g]d: Plate Thickness, [mm]Source: I TO, Y. e outros: Weldability Formula of High Strength Steels. I.I.W. Document IX-576-68.Yurioka.[]07502520012=+−A C C(),,tanh(,)Notation:C EQ_Yurioka: Equivalent Carbon for Pipeline Steels [%]Alloy Content: [weight %]Notes:- Formula for C-Mn and microalloyed pipeline steels- This formula combines Carbon Equivalent equations from IIW and P cmSource: P ATCHETT, B.M. et al.: Casti Metals Blue Book: Welding Filler Metals. Casti Publishing Corp., Edmonton, February 1993, 608 p. (CD Edition).- Equivalent Carbon – Bake Hardenability CapabilityMelco.Notation:C eq_bh: Equivalent Carbon Expressed As Bake Hardenability [%]Alloy Content: [weight %]Source: M itsubishi Electric Co., 1998.- Hot Strength of Steel. Tselikov2013792 E+−CCSi+=+Mn−+−−T17400012000P6,,05289225S308250T 4292414400020525Notation:E: Young Modulus [kgf/cm²]C: C content [weight %]Mn: Mn content [weight %]Si: Si content [weight %]P: P content [weight %]S: S content [weight %]T:Temperature [°C]Note:- Valid for carbon, alloy and stainless steels between 20 and 900°C.Source: ROYZMAN, S.E. Thermal Stresses in Slab Solidification. Asia Steel, 1996, 158-162.. MisakaNotation:σ: Steel Hot Strength [kgf/mm²]C: C content [weight %]T: Absolute Temperature [K]ε: True Straint: Time [s]Source: MISAKA, Y. et al. Formulatization of Mean Resistance to Deformation of Plain C Steels at Elevated Temperature.Journal of the Japan Society for the Technology of Plasticity, 8, 79, 1967-1968, 414-422.. ShidaCalculation algorithm expressed in Visual Basic:Function Shida(C, T, Def, VelDef)Dim nShida, Td, g, Tx, mShida, SigF As SinglenShida = 0.41 – 0.07 * CTd = 0.95 * (C + 0.41) / (C + 0.32)T = (T + 273) / 1000If T >= Td Theng = 1Tx = TmShida = (-0.019 * C + 0.126) * T + (0.075 * C – 0.05)Elseg = 30 * (C + 0.9) * (T – 0.95 * (C + 0.49) / (C + 0.42)) ^ 2 + (C + 0.06) / (C + 0.09)Tx = TdmShida = (0.081 * C – 0.154) * T + (-0.019 * C + 0.207) + 0.027 / (C + 0.32)End IfSigF = 0.28 * g * Exp(5 / Tx – 0.01 / (C + 0.05))Shida = 2 / Sqr(3) * SigF * (1.3 * (Def / 0.2) ^ nShida – 0.3 * (Def / 0.2)) * _(VelDef / 10) ^ mShidaEnd FunctionNotation:σ: Steel Hot Strength [kgf/mm²]C: C content [weight %]T: Temperature [°C]Def: True StrainVelDef: Strain Rate [s-1]Source: SHIDA, S. Effect of Carbon Content, Temperature and Strain Rate on Flow Stress of Carbon Steels.Hitachi Technical Report, 1974, 14 p.- Liquidus Temperature of Steels[]T C Si Mn P S Cu Ni Cr Al Mo V Ti Liq =−+++++++++++1536787649343053113362218,,,,,Notation:T Líq : Steel Melting Temperature [°C]Alloy Content : [weight %]Source: GUTHMANN, K. Stahl und Eisen , 71(1951), 8, 399-402.- Niobium Solubilization in Microalloyed Steels. IrvineNotation:T : Temperature [°C]Alloy Content : [weight %]Source: I RVINE, K.J. et al.: Journal of the Iron and Steel Institute , 205, 1967, 161.. SicilianoNotation:T : Temperature [°C]Alloy Content : [weight %]Source: S ICILIANO JR., F..: Mathematical Modeling of the Hot Strip Rolling of Nb Microalloyed Steels Ph.D. Thesis ,McGill University, February 1999, 165 p.- Relationships Between Chemical Composition x Microstructure x Mechanical Properties. C-Mn Steelsεunif sol Perl Mn Si Sn N =−−−−−027001600150040004310,,,,,,Notation:LE: Yield Strength at 0,2% Real Strain [MPa]LR: Tensile Strength [MPa]dσ/dε: Strain Hardening Coefficient at 0,2% Real Strain [1/MPa]εunif: Uniform Elongation, Expressed as Real (Logarithmic) Strainεtot: Total Elongation, Expressed as Real (Logarithmic) StrainPerl: Pearlite Fraction in Microstructure [%]T trans: Fracture Appearance Transition Temperature [°C]Alloy Content: [weight %]d: Grain Size [µm]Source: P ICKERING, F.B.: The Effect of Composition and Microstructure on Ductility and Toughness; in: Towards Improved Ductility and Toughness, Climax Molybdenum Company, Tokyo, 1971, p. 9-32Notation:LE: Yield Strength at 0,2% Real Strain [MPa]LR: Tensile Strength [MPa]Perl: Pearlite Fraction Present in Microstructure [%]Alloy Contents: [weight %]d: Grain Size [µm]Source: P ICKERING, F.B.: Physical Metallurgy and the Design of Steels. Allied Science Publishers, London, 1978, 275 p.Notation:50% ITT: Impact Transition Temperature for 50% Tough Fracture [°C]Perl: Pearlite Fraction Present in Microstructure [%]Alloy Contents: [weight %]d: Grain Size [µm]Source: PICKERING, F.B. & GLADMAN, T.: In Metallurgical Developments in Carbon Steels. The iron and Steel Institute, London, 1961, 10-20. V-Ti-N Steels Processed by Recrystallization Controlled RollingNotation:LE: Yield Strength at 0,2% Real Strain [MPa]LR: Tensile Strength [MPa]Alloy Content: [weight %]h f: Plate Thickness [mm]Notes:- Formula Derived for Steels with Al Content over 0,010% and Si Content between 0,25 and 0,35%.- Precision of the formulas: ± 40 MPa.Source: M ITCHELL, P.S. et al.: In: Low Carbon Steels for the 90’s. Proceedings. American Society for Metals/The Metallurgical Society, Pittsburgh, Oct. 1993..Dual Phase SteelsSource: G ORNI, A.A.: Efeito da Temperatura de Acabamento e Velocidade de Resfriamento na Microestrutura e Propriedades Mecânicas de um Aço Bifásico ao Mn-Si-Cr-Mo; Dissertação de Mestrado, Departamento de Engenharia Metalúrgica e de Materiais da Escola Politécnica da Universidade de São Paulo, São Paulo, 1989, 184 p.NotationLE: Yield Strength [MPa]LR: Tensile Strength [MPa]dσ/dε: Strain Hardening Coefficient at Uniform Elongation [1/MPa]a unif: Uniform Elongation [%]Lαα: Mean Ferritic Free Path [µm]dβ: Mean Diameter of Martensite Islands [µm]- Solidus Temperature of Steels[]Al Cr Ni S P Mn Si C T Sol 1,44,13,49,1835,1248,63,125,4151536+++++++−=Notation:T Líq : Steel Melting Temperature [°C]Alloy Content : [weight %]Source: TAKEUCHI, E. & BRIMACOMBE, J.K. Effect of Oscillation-Mark Formation on the Surface Quality of ContinuouslyCast Steel Slabs . Metallurgical Transactions B , 16B, 9, 1985, 605-25.USEFUL DATA AND CONSTANTS - Steel Scale Density: 4,86 g/cm³ (Combustol)GENERAL STATISTICAL FORMULAS- Correlation CoefficientNotation:r : Correlation CoefficientY : Raw DataY est : Estimated Data Calculated by the Fitted EquationY _: Mean of the Raw DataSource: SPIEGEL, M.R. Estatística , Editora McGraw-Hill do Brasil Ltda., São Paulo, 1976, 580 p.- Standard Error of EstimationNotation:σ: Standard Error of EstimationY est : Estimated Data Calculated by the Fitted EquationY _: Mean of the Raw Datan : Number of Points of DataSource: SPIEGEL, M.R. Estatística , Editora McGraw-Hill do Brasil Ltda., São Paulo, 1976, 580 p.。
NB对低碳钢焊接区组织和性能的影响作者：牟世超马新新于腾飞来源：《科学导报·科学工程与电力》2019年第07期【摘要】介绍了冷金属过渡+脉冲（CMT+P）焊接的焊接方法和特点.采用CMT+P焊接工艺对低碳钢板进行了对接焊接试验，并对比分析了低碳钢的CMT+P焊接工艺与TIG打底+SMAW填充焊焊接工艺的焊接接头组织和性能.结果表明，两种工艺的焊接接头经热处理后均为回火马氏体组织，且CMT+P的马氏体板条间距较小，热影响区为等轴晶且较窄，高温蠕变性能相对较好；CMT+P焊接接头抗拉强度优于母材，且冲击韧性与TIG打底+SMAW填充焊焊接头冲击韧性水平相当.进而证实了CMT+P可作为低碳钢焊接工艺的一种新选择.【关键词】低碳钢；冷金属过渡+脉冲焊；焊接接头；金相组织；力学性能中图分类号：TG444 文献标识码：A引言低碳钢是一种新型马氏体耐热钢，具有高温强度高、导热性好、热膨胀系数低和蠕变性能好等优点.低碳钢主要用于超超临界机组的高温、高压主蒸气管道等部件，其焊接接头的性能对机组的安全运行至关重要.目前，工程应用中低碳钢的焊接工艺是TIG打底、SMAW焊填充、盖面.TIG打底焊虽然焊接接头强韧性好，但焊接速度不高，焊丝熔敷率低，影响焊接效率.SMAW焊接效率虽高，但焊接热输入大，焊缝组织晶粒粗大，焊接热影响区较宽.而且其电弧穿透力差，焊缝熔深小.所以，SMAW焊接接头力学性能不够优异.CMT是一种新型焊接方法，它是在MIG/MAG焊的基础上通过焊丝回抽使熔滴在短路过渡电流接近于零的情况下实现短路过渡.CMT既能降低焊接热输入，又能提高焊接效率.但由于CMT热输入低，不适合3mm 以上厚板的焊接.而CMT+P是在CMT基础上开发的能够更大范围控制热输入的焊接方法，可用于厚铝板的焊接.文中为了探索CMT+P是否可以替代TIG打底+SMAW填充的焊接方法用于P92钢焊接以提高焊接效率获得组织性能优异的焊接接头，采用CMT+P对15mm厚低碳钢板进行了对接试验，并研究了对接接头的组织性能，进一步促进低碳钢在工业中进一步的应用.1、试验方法试验焊机为FroniusCMTAdvanced4000，焊接机器人为FANUCRobotM-10iA，用NIUSB−6361数据采集卡采集焊接电流电压信号.焊丝直径为φ1.2mm的OerlikonCarbofilCrMo92实芯焊丝.平板对接母材规格为150mm×85mm×15mm，坡口形式及尺寸如图1所示.焊接过程采用Ar+2.5%CO2混合气体保护，气流量15L/min.2、结果及讨论2.1强化处理对焊接接头抗拉性能的影响图2所示。
