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CN109136485A - The manufacturing method of automobile stabilizer bar unimach and stabiliser bar - Google Patents

The manufacturing method of automobile stabilizer bar unimach and stabiliser bar Download PDF

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Publication number
CN109136485A
CN109136485A CN201811157456.3A CN201811157456A CN109136485A CN 109136485 A CN109136485 A CN 109136485A CN 201811157456 A CN201811157456 A CN 201811157456A CN 109136485 A CN109136485 A CN 109136485A
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stabilizer bar
steel
automobile
manufacturing
temperature
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Inventor
代文杰
徐驰
潘诗琰
申小平
范沧
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Nanjing University of Science and Technology
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Nanjing University of Science and Technology
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Priority to CN201811157456.3A priority Critical patent/CN109136485A/en
Publication of CN109136485A publication Critical patent/CN109136485A/en
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    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/26—Methods of annealing
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/002—Heat treatment of ferrous alloys containing Cr
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/008—Heat treatment of ferrous alloys containing Si
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/10—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of tubular bodies
    • C21D8/105—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of tubular bodies of ferrous alloys
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/08—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for tubular bodies or pipes
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C33/00—Making ferrous alloys
    • C22C33/04—Making ferrous alloys by melting
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/002—Bainite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/008—Martensite

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Manufacturing & Machinery (AREA)
  • Heat Treatment Of Steel (AREA)

Abstract

本发明公开了一种汽车稳定杆用超高强度钢及稳定杆制造方法，以重量百分比计，稳定杆用钢化学成分为：C 0.20%~0.50%，Mn 0.50%~3.0%，Cr 0.01%~0.45%，Al 0.015%~0.07%，Si 0.20%~1.35%，B 0.001%~0.006%，V+Ti 0.01~1.20%，余为Fe和不可避免的杂质。稳定杆制造方法为：依次进行转炉或电炉冶炼‑炉外精炼‑连铸连轧‑斜轧穿孔‑多道次冷拔‑热处理‑稳定杆总成制作。用本发明钢和制造方法制造的稳定杆金相组织为贝氏体+板条马氏体+残余奥氏体+孪晶马氏体的复相组织，其屈服强度Rp0.2≥1400Mpa，抗拉强度Rm≥1600MPa，断后延伸率A≥10%。本发明稳定杆强韧性综合力学性能远优于现有钢种，充分满足稳定杆类弹性件的力学性能要求，可减少稳定杆钢材用量，实现汽车轻量化。

The invention discloses an ultra-high-strength steel for an automobile stabilizer bar and a manufacturing method for the stabilizer bar. In terms of weight percentage, the chemical composition of the steel for the stabilizer bar is: C 0.20%-0.50%, Mn 0.50%-3.0%, Cr 0.01% ~0.45%, Al 0.015%~0.07%, Si 0.20%~1.35%, B 0.001%~0.006%, V+Ti 0.01~1.20%, the rest is Fe and inevitable impurities. The manufacturing method of the stabilizer bar is as follows: converter or electric furnace smelting, out-of-furnace refining, continuous casting and rolling, skew rolling and piercing, multi-pass cold drawing, heat treatment, and stabilizer bar assembly fabrication. The metallographic structure of the stabilizer bar manufactured by the steel and the manufacturing method of the present invention is a complex structure of bainite + lath martensite + retained austenite + twinned martensite, and its yield strength R p0.2 ≥ 1400Mpa, Tensile strength R m ≥ 1600MPa, elongation after fracture A ≥ 10%. The comprehensive mechanical properties of strength and toughness of the stabilizer bar of the invention are far superior to the existing steel types, fully meet the mechanical property requirements of the stabilizer bar type elastic parts, can reduce the steel consumption of the stabilizer bar, and realize the lightweight of the automobile.

Description

The manufacturing method of automobile stabilizer bar unimach and stabiliser bar
Technical field
The invention belongs to steel alloy and steel pipe manufacturing fields, and in particular to a kind of automobile stabilizer bar unimach and steady Fixed pole manufacturing method.
Background technique
Automobile stabilizer bar be in order to prevent automobile turning when the torque arm that laterally topples, be typically secured to automobile chassis or so The lower arm of suspension.With resource, the increasingly increase of the energy, environmental pressure, lightweight is realized under the premise of guaranteeing vehicle performance Have become the trend of current automotive industry.Automobile stabilizer bar uses high-intensitive and high-ductility hollow component to reduce steel Dosage is one of effective way of automobile lightweight.
In recent years for energy saving, simplified process, automobile and the higher components of mechanical performance requirement are developed in succession The new materials such as non-hardened and tempered steel, air-cooled bainitic steels out, but using less in spring-like product.Such as Publication No. CN 102899589A " a kind of high intensity non quenched and tempered bainitic steel and preparation method " is that quick air-cooled obtaining portion is divided after crankshaft forging The method that bainite structure replaces quenched steel crankshaft.Although having added a variety of noble elements such as Mo, V, Cr in steel, obtained because final Tissue obdurability deficiency (the tensile strength R arrivedm>=1085MPa, yield strength Rp0.2>=795MPa), it is not able to satisfy stabiliser bar class The mechanical property requirements of elastic component.The requirement of spring product is also not achieved in the mechanical property of most high tough air-cooled bainitic steels, Some then containing there are many noble element or rare element (such as Mo, Ni, V) of high level, keeps material cost very high and is difficult to Practical application.The patent " air-cooled bainite steel with high toughness and high quenching performance " of publication number CN 1078269A emphasizes high-hardenability, Large-sized part natural cooling in air, i.e. cooling rate >=1 DEG C/min between 900 DEG C ~ 300 DEG C are asked, but is Guarantee harden ability and the content for improving the elements such as Mn, Si of having to, to be also added the noble elements such as Mo, V, material cost compared with It is high.In addition, the part air-cooled required time is very long, the Automotive Stabilizer Bar for requiring short cycle to produce in enormous quantities is made to be difficult to obtain Practical application.Publication number Cn 105088081A " manufacturing process of stabiliser bar bainite and martensite spring steel and stabiliser bar ", Cooling obtain of control is used to add part low-carbon martensite and a small amount of retained austenite with bainite after being heated to 900 DEG C ~ 1050 DEG C, Then lonneal makes material mechanical performance reach Rm>=1350MPa, yield strength Rp0.2>=1050MPa, elongation after fracture A >= 10%, contraction percentage of area Z >=35%.However its intensity is still lower, it is difficult to meet the needs of automotive light weight technology.
Summary of the invention
The purpose of the present invention is in view of the above technical problems, by ingredient design and thermomechanical treatment process, form crystal grain The fine uniform and tough automobile of height being made of bainite/lath martensite/retained austenite/lamellar martensite heterogeneous structure is steady Fixed pole.
To achieve the object of the present invention, change of the automobile stabilizer bar of the present invention with unimach comprising following weight percent It studies point: C 0.20% ~ 0.50%, Mn 0.50% ~ 3.0%, Cr 0.01% ~ 0.45%, Al 0.015% ~ 0.07%, Si 0.20% ~ 1.35%, B 0.001% ~ 0.006%, V+Ti 0.01 ~ 1.20%, remaining is Fe and inevitable impurity.
Preferably, the chemical composition comprises the following components in percentage by weight of automobile stabilizer bar unimach of the present invention are as follows: C 0.35% ~ 0.40%, Mn 2.1% ~ 2.5%, Cr 0.18% ~ 0.27, Al 0.04% ~ 0.06%, Si 1.20 ~ 1.35%, B 0.004 ~ 0.006%, V 0.04 ~ 0.05, Ti 0.03 ~ 0.04.
The manufacturing process of automobile unimach stabiliser bar of the present invention, comprising the following steps:
(1) raw material for constituting the chemical component of the unimach successively carry out converter or electric furnace smelting, the refining of LF furnace and VD furnace vacuum outgas；
(2) the molten steel continuous casting and rolling of refining gained is at round steel billet, and removes surface folding and defect；
(3) roll piercing is carried out to round steel billet and determines tube reducing；
(4) annealing and pickling；
(5) 3 ~ 5 passage cold-drawns and 1 passage empty sinking are carried out, is made annealing treatment after cold-drawn each time；
(6) it is heat-treated.
Further, in step (3), roll piercing temperature is 1100 DEG C ~ 1250 DEG C, drafts 10 ~ 25%.
Further, in step (4), specific steps are made annealing treatment are as follows: first by steel pipe in 760 DEG C ~ 850 DEG C heat preservation 1h ~ 5h, Afterwards in 650 DEG C ~ 780 DEG C heat preservation 1h ~ 5h；Pickling use concentration for 4% ~ 25% hydrochloric acid or sulfuric acid.
Further, in step (5), 3 passage cold-drawns are carried out, wherein the deflection and mill speed of cold-drawn are respectively 14% ~17%,2m/min；20%~21%,2.5m/min；24% ~ 25%, 3m/min, the deflection and mill speed of empty sinking be 22% ~ 23%, 3m/min.The temperature of cold-drawn after annealing processing each time is 700 DEG C ~ 780 DEG C, soaking time 1h ~ 5h.
Further, in step (6), specific steps are heat-treated are as follows: steel pipe is heated to Ac1 or more 20 DEG C ~ 100 first DEG C, 5min ~ 30min is kept the temperature, subsequent air accelerates cooling or water cooling to 250 DEG C ~ 450 DEG C, keeps the temperature 30mim ~ 150min, last empty Gas accelerates cooling or water cooling.
The design considerations of chemical composition and critical process of the invention is as follows:
C is the most frequently used also most effective intensified element in steel, is played a role by gap solution strengthening and Carbide Precipitation reinforcing. Carbon content is designed in the present invention between 0.20% ~ 0.50%, by being quickly cooled to one between Ms point and Mf point after austenitizing Determine temperature, obtains lath martensite and bainite and a small amount of retained austenite of appropriate level.In this temperature, promote carbon first Element improves stabilization of austenite from being spread in oversaturated martensite and bainite to retained austenite.Finally it is quickly cooled to Room temperature makes the lamellar martensite of retained austenite portions turn high-carbon to improve intensity, partially remains and subsequent Cold working or military service deformation process in deformation occurs induced phase transition and improve plasticity and toughness.C content is too low can not to form enough numbers The martensite and bainite of amount, intensity is insufficient, too high, reduces plasticity and welding performance.
The intensity and harden ability of matrix can be improved in the addition of Mn element in steel of the present invention, and by reducing the refinement of Ac3 temperature Crystal grain after cooling, in addition, Mn also improves austenite content and stability as austenite former, so as to improve modeling Toughness.But excessively high Mn content makes serious steel billet segregation, thermal stress and big, the weldability decline of structural stress etc., designs accordingly Mn content is between 0.50% ~ 3.0%.
A small amount of Cr and B element ensure that the harden ability of steel, make steel that can also form sufficient amount of plate under the conditions of air-cooled Martensite and bainite.However excessive Cr keeps steel firmly crisp, therefore by the control of Cr content between 0.01% ~ 0.45%.
Si can be strengthened by way of gap is dissolved, to improve tensile strength and yield strength simultaneously.Si can be shown The formation for hindering carbide is write, the fine-scale of carbide is on the one hand realized, on the other hand guarantees that enough C elements diffuse to In austenite.Crackle tendency when Si too high levels make Tube Drawing improves, and deteriorates welding performance, and easily lead to it is cold short, accordingly The Si content of design is between Si 0.20% ~ 1.35%.
V and Ti element can form tiny carbide and be strengthened, and hinder grain coarsening, and steel is made to keep small grains ruler Degree.
The stabiliser bar produced using automobile stabilizer bar unimach of the present invention and stabiliser bar manufacturing method, passes through low-carbon Lath martensite, bainite and high-carbon lamellar martensite are strengthened, and are mentioned by the phase transformation effect of retained austenite High-plasticity.Compared with prior art, the splendid matching of obdurability is realized, comprehensive mechanical property is much better than existing steel grade, fills Divide the mechanical property requirements for meeting stabiliser bar class elastic component, stabiliser bar rolled steel dosage, automobile lightweight can be reduced.
Detailed description of the invention
Fig. 1 is the SEM scanning electricity of the automobile stabilizer bar unimach matrix of 1 manufacture according to embodiments of the present invention Mirror figure.
Fig. 2 is engineering stress-strain curve of the automobile stabilizer bar unimach of 1 manufacture according to embodiments of the present invention Figure.
Specific embodiment
Below according to specific embodiment, technical scheme is described further.Protection scope of the present invention is unlimited In following embodiment, these embodiments are enumerated merely for exemplary purpose without limiting the invention in any way.
Embodiment 1
It successively carries out electric furnace smelting, the refining of LF furnace, the vacuum outgas of VD furnace and continuous casting and rolling and automobile stabilizer bar superhigh intensity is made Steel round blank, chemical composition are C 0.39%, Mn 2.21%, Cr 0.25%, Al 0.06%, Si 1.33%, B 0.005%, V 0.04, Ti 0.04%.In 1200 DEG C of roll piercings, drafts 20% directly determines tube reducing after perforation.Hereafter it is made annealing treatment simultaneously Pickling: first by steel pipe after 800 DEG C of heat preservation 1.5h in 720 DEG C of heat preservation 1h；Pickling use concentration for 10%% hydrochloric acid or sulfuric acid.It is right Steel pipe carries out 3 passage cold-drawns, and pass deformation and mill speed are respectively 14%, 20%, 24%；2mm/min,2.5mm/min, 3mm/min, and made annealing treatment after cold rolling every time.Steel pipe is heated to 930 DEG C, keeps the temperature 12min, subsequent water cooling to 350 DEG C, keep the temperature 150min, rear water cooling to room temperature.Finally stabiliser bar assembly is made by existing conventional stabiliser bar assembly production method.
The stabiliser bar matrix of the present embodiment production is lath martensite, lamellar martensite and retained austenite, is averaged Less than 10 μm (see figure 1)s of crystallite dimension.Water cooling makes austenite fraction mutually become lath martensite, portion to 320 DEG C after austenitizing Code insurance is left retained austenite, and subsequent isothermal heat preservation expands oversaturated carbon in lath martensite into residual austenite body It dissipates, last water cooling makes portion of residual austenite be changed into lamellar martensite, and part retains to room temperature, final residual austenite content About 9.2%.The generation of high-carbon lamellar martensite is so that the intensity of material is further increased compared to single lath martensite, inversion The elements such as austenite richness C, Mn, thermodynamic stability is good, martensitic traoformation does not occur in cooling procedure, but in deformation process Martensitic traoformation occurs, the generation in advance of dissipation energy, the generation and constriction that avoid micropore is dropped simultaneously so as to improve plasticity and toughness Low yield strength ratio.The stress-strain diagram of the present embodiment unimach is as shown in Fig. 2, its mechanical property are as follows: tensile strength 1756MPa, yield strength 1447MPa, elongation percentage 13.2%.
Embodiment 2
For other steps with embodiment 1, steel pipe chemical composition is C 0.48%, Mn 1.34%, Cr 0.40%, Al 0.037%, Si 0.76%, B 0.005%, V 0.07, Ti 0.02%.Steel pipe is heated to 920 DEG C after cold-drawn, keeps the temperature 15min, subsequent water It is cooled to 250 DEG C, keeps the temperature 60min, last water cooling to room temperature.Its residual austenite content about 4.5%, tensile strength 1774MPa are bent Take intensity 1468MPa, elongation percentage 10.4%.
Embodiment 3
For other steps with embodiment 1, steel pipe chemical composition is C 0.21%, Mn 0.50%, Cr 0.28%, Al 0.042%, Si 1.35%, B 0.004%, V 0.08.Steel pipe is heated to 950 DEG C after cold-drawn, keeps the temperature 5min, subsequent water cooling to 380 DEG C, Keep the temperature 120min, last water cooling to room temperature.Its residual austenite content about 9.1%, tensile strength 1658MPa, yield strength 1453MPa, elongation percentage 14.2%.
Embodiment 4
For other steps with embodiment 1, steel pipe chemical composition is C 0.35%, Mn 2.96%, Cr 0.37%, Al 0.045%, Si 1.20%, B 0.004%, V 0.02, Ti 0.03.Steel pipe is heated to 920 DEG C after cold-drawn, keeps the temperature 20min, subsequent water cooling To 320 DEG C, 30min, last water cooling to room temperature are kept the temperature.Its residual austenite content about 7.5%, tensile strength 1742MPa, surrender Intensity 1453MPa, elongation percentage 12.4%.
Embodiment 5
For other steps with embodiment 1, steel pipe chemical composition is C 0.28%, Mn 1.45%, Cr 0.02%, Al 0.07%, Si 0.89%, B 0.005%, V 0.07, Ti 0.01.Steel pipe is heated to 900 DEG C after cold-drawn, keeps the temperature 20min, subsequent water cooling is extremely 280 DEG C, keep the temperature 45min, last water cooling to room temperature.Its residual austenite content about 6.8%, tensile strength 1635MPa, surrender are strong Spend 1428MPa, elongation percentage 13.3%.
Comparative example 1
For other steps with embodiment 1, steel pipe chemical composition is C 0.15%, Mn 0.75%, Cr 0.04%, Al 0.052%, Si 1.21%, B 0.006%, V 0.06, Ti 0.03.Steel pipe is heated to 920 DEG C after cold-drawn, keeps the temperature 10min, subsequent water cooling To 300 DEG C, 40min, last water cooling to room temperature are kept the temperature.Its carbon content is less, and the lath martensite intensity of formation is insufficient, does not have simultaneously There are enough carbon stable austenites, residual austenite content is few, and is difficult to form lamellar martensite, and tensile strength 1451MPa is bent Take intensity 1245MPa, elongation percentage 10.2%.
Comparative example 2
For other steps with embodiment 1, steel pipe chemical composition is C 0.43%, Mn 0.82%, Cr 0.03%, Al 0.031%, Si 1.26%, B 0.004%, V 0.08.Steel pipe is heated to 1000 DEG C after cold-drawn, keeps the temperature 10min, subsequent water cooling to 320 DEG C, keep the temperature 45min, last water cooling to room temperature.Since austenitizing temperature is excessively high, crystal grain is roughened, and after austenitizing Quenching structure in start to generate lamellar martensite, the lamellar martensite generated in size and retained austenite mutually becomes apparent slightly Change, thus damages plasticity, tensile strength 1724MPa, yield strength 1467MPa, elongation percentage 6.7%.
Comparative example 3
For other steps with embodiment 1, steel pipe chemical composition is C 0.30%, Mn 2.11%, Cr 0.36%, Al 0.04%, Si 1.02%, B 0.004%, V 0.06%.Steel pipe is heated to 920 DEG C after cold-drawn, keeps the temperature 12min, subsequent water cooling is protected to 200 DEG C Warm 50min, last water cooling to room temperature.Its matrix is lath martensite and a small amount of retained austenite, and austenite content is about 1.3%, tensile strength 1526MPa, yield strength 1468MPa, elongation percentage 8.9%.
Comparative example 4
For other steps with embodiment 1, steel pipe chemical composition is C 0.24%, Mn 1.73%, Cr 0.35%, Al 0.06%, Si 0.75%, B 0.002%, V 0.04, Ti 0.04.Steel pipe is heated to 920 DEG C after cold-drawn, keeps the temperature 15min, subsequent water cooling is extremely 450 DEG C, keep the temperature 30min, last water cooling to room temperature.Its matrix is single bainite, tensile strength 968MPa, yield strength 744MPa, elongation percentage 16.8%.
The stabiliser bar that automobile stabilizer bar unimach of the present invention and stabiliser bar manufacturing method provide, by lath horse The retained austenite of high-intensitive lamellar martensite and high tenacity is further introduced on family name's body/bainite matrix to improve mechanical property Can, yield strength Rp0.2>=1400Mpa, tensile strength Rm>=1600MPa, elongation after fracture A >=10%, the comprehensive mechanics of obdurability Performance is much better than existing steel grade, sufficiently meets the mechanical property requirements of stabiliser bar class elastic component, can reduce stabiliser bar rolled steel dosage, Automobile lightweight.
By the mechanical property induction and contrast such as table 1 of steel obtained by embodiment 1-5 and comparative example 1-4, it is possible to find side of the present invention Stabiliser bar steel comprehensive mechanical property obtained by case is outstanding.
1 embodiment of table is compared with stabiliser bar obtained by comparative example with steel mechanical property
Embodiment Tensile strength (MPa) Yield strength (Mpa) Elongation percentage (%)
Embodiment 1 1756 1447 13.2
Embodiment 2 1774 1468 10.4
Embodiment 3 1658 1453 14.2
Embodiment 4 1742 1453 12.4
Embodiment 5 1635 1428 13.3
Comparative example 1 1451 1245 10.2
Comparative example 2 1724 1467 6.7
Comparative example 3 1526 1468 8.9
Comparative example 4 968 744 16.8

Claims (10)

1.一种汽车稳定杆用超高强度钢，其特征在于，以重量百分比计，其化学成分为：C0.20%~0.50%，Mn 0.50%~3.0%，Cr 0.01%~0.45%，Al 0.015%~0.07%，Si 0.2%~1.35%， B0.001%~0.006%，V+Ti 0.01~1.2%，余量为Fe和不可避免的杂质。1. an ultra-high-strength steel for an automobile stabilizer bar, characterized in that, by weight percentage, its chemical composition is: C0.20%～0.50%, Mn 0.50%～3.0%, Cr 0.01%～0.45%, Al 0.015%~0.07%, Si 0.2%~1.35%, B0.001%~0.006%, V+Ti 0.01~1.2%, the balance is Fe and inevitable impurities. 2.一种汽车稳定杆用超高强度钢，其特征在于，以重量百分比计，其化学成分为：C0.35%~0.40%，Mn 2.1%~2.5%，Cr 0.18%~0.27，Al 0.04%~0.06%，Si 1.20~1.35%，B 0.004~0.006%，V 0.04~0.05，Ti 0.03~0.04。2. An ultra-high-strength steel for an automobile stabilizer bar, characterized in that, by weight percentage, its chemical composition is: C0.35%～0.40%, Mn 2.1%～2.5%, Cr 0.18%～0.27, Al 0.04 %~0.06%, Si 1.20~1.35%, B 0.004~0.006%, V 0.04~0.05, Ti 0.03~0.04. 3.利用权利要求1或2所述的超高强度钢制造的汽车稳定杆。3. An automobile stabilizer bar made of the ultra-high-strength steel according to claim 1 or 2. 4.如权利要求3所述的汽车稳定杆的方法，其特征在于，经过如下步骤：4. The method for an automobile stabilizer bar as claimed in claim 3, characterized in that, through the following steps: （1）使所述超高强度钢的化学成分构成的原料依次进行转炉或电炉冶炼、LF炉精炼和VD炉真空脱气；(1) The raw material composed of the chemical composition of the ultra-high strength steel is sequentially subjected to converter or electric furnace smelting, LF furnace refining and VD furnace vacuum degassing; （2）步骤（1）所得钢水连铸连轧成圆钢坯，并清除表面褶皱和缺陷；(2) The molten steel obtained in step (1) is continuously cast and rolled into a round billet, and surface wrinkles and defects are removed; （3）对圆钢坯进行斜轧穿孔和定减径；(3) Cross-rolling, piercing and diameter reduction of round billets; （4）退火处理并酸洗；(4) annealing and pickling; （5）进行3~5道次冷拔和1道次空拔，每一次冷拔之后进行退火处理；(5) 3~5 passes of cold drawing and 1 pass of air drawing are carried out, and annealing treatment is carried out after each cold drawing; （6）进行热处理。(6) heat treatment. 5.如权利要求4所述的方法，其特征在于，步骤（3）中，所述斜轧穿孔温度为1100℃~1250℃，压下量10~25%。5 . The method of claim 4 , wherein, in step (3), the temperature of the cross-rolling and piercing is 1100°C to 1250°C, and the reduction is 10 to 25%. 6 . 6.如权利要求4所述的方法，其特征在于，步骤（4）中，退火处理步骤为：先将钢管在760℃~850℃保温1h~5h，后于650℃~780℃保温1h~5h；酸洗采用浓度为4%~25%的盐酸或硫酸。6 . The method of claim 4 , wherein in step (4), the annealing treatment step is: firstly, the steel pipe is kept at 760°C-850°C for 1h-5h, and then kept at 650°C-780°C for 1h-5. 7 . 5h; pickling adopts hydrochloric acid or sulfuric acid with a concentration of 4%~25%. 7.如权利要求4所述的方法，其特征在于，步骤（5）中，进行3道次冷拔，其中，冷拔的变形量和轧制速度分别为14%~17%、2m/min；20%~21%、2.5m/min；24%~25%、3m/min。7 . The method of claim 4 , wherein in step (5), 3 passes of cold drawing are performed, wherein the deformation amount and rolling speed of cold drawing are 14%-17%, 2 m/min, respectively. 8 . ; 20%~21%, 2.5m/min; 24%~25%, 3m/min. 8.如权利要求4所述的方法，其特征在于，步骤（5）中，空拔的变形量和轧制速度为22%~23%、3m/min。8 . The method according to claim 4 , wherein in step (5), the deformation amount and rolling speed of the empty drawing are 22%-23% and 3 m/min. 9 . 9.如权利要求4所述的方法，其特征在于，步骤（5）中，退火处理温度为700℃~780℃，保温时间1h~5h。9 . The method of claim 4 , wherein, in step (5), the annealing temperature is 700° C. to 780° C., and the holding time is 1 h to 5 h. 10 . 10.如权利要求4所述的方法，其特征在于，其特征在于，步骤（6）中，所述热处理具体步骤为：首先将钢管加热至Ac1以上20℃~100℃，保温5min~30min，随后空气加速冷却或水冷至250℃~450℃，保温30mim~150min，最后空气加速冷却或水冷。10 . The method of claim 4 , wherein, in step (6), the specific steps of the heat treatment are: firstly heating the steel pipe to 20°C to 100°C above Ac1, keeping the temperature for 5min to 30min, 11 . Then air-accelerated cooling or water-cooling to 250℃~450℃, heat preservation for 30mim~150min, and finally air-accelerated cooling or water-cooling.
CN201811157456.3A 2018-09-30 2018-09-30 The manufacturing method of automobile stabilizer bar unimach and stabiliser bar Pending CN109136485A (en)

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