WO2020078007A1 - 一种高强高韧性非调质圆钢及制备方法 - Google Patents

一种高强高韧性非调质圆钢及制备方法 Download PDF

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WO2020078007A1
WO2020078007A1 PCT/CN2019/089346 CN2019089346W WO2020078007A1 WO 2020078007 A1 WO2020078007 A1 WO 2020078007A1 CN 2019089346 W CN2019089346 W CN 2019089346W WO 2020078007 A1 WO2020078007 A1 WO 2020078007A1
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quenched
rolling
round steel
cooling
controlled
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PCT/CN2019/089346
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English (en)
French (fr)
Inventor
周蕾
刘文学
孙华
张�浩
田杰平
魏刚武
杨伟宁
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南京钢铁股份有限公司
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Priority to EP19872447.8A priority Critical patent/EP3859042A4/en
Publication of WO2020078007A1 publication Critical patent/WO2020078007A1/zh

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    • 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
    • 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
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • C21D1/25—Hardening, combined with annealing between 300 degrees Celsius and 600 degrees Celsius, i.e. heat refining ("Vergüten")
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
    • B22D11/12—Accessories for subsequent treating or working cast stock in situ
    • B22D11/1206—Accessories for subsequent treating or working cast stock in situ for plastic shaping of strands
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21C—PROCESSING OF PIG-IRON, e.g. REFINING, MANUFACTURE OF WROUGHT-IRON OR STEEL; TREATMENT IN MOLTEN STATE OF FERROUS ALLOYS
    • C21C7/00—Treating molten ferrous alloys, e.g. steel, not covered by groups C21C1/00 - C21C5/00
    • C21C7/0056—Treating molten ferrous alloys, e.g. steel, not covered by groups C21C1/00 - C21C5/00 using cored wires
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21C—PROCESSING OF PIG-IRON, e.g. REFINING, MANUFACTURE OF WROUGHT-IRON OR STEEL; TREATMENT IN MOLTEN STATE OF FERROUS ALLOYS
    • C21C7/00—Treating molten ferrous alloys, e.g. steel, not covered by groups C21C1/00 - C21C5/00
    • C21C7/04—Removing impurities by adding a treating agent
    • C21C7/06—Deoxidising, e.g. killing
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21C—PROCESSING OF PIG-IRON, e.g. REFINING, MANUFACTURE OF WROUGHT-IRON OR STEEL; TREATMENT IN MOLTEN STATE OF FERROUS ALLOYS
    • C21C7/00—Treating molten ferrous alloys, e.g. steel, not covered by groups C21C1/00 - C21C5/00
    • C21C7/04—Removing impurities by adding a treating agent
    • C21C7/064—Dephosphorising; Desulfurising
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21C—PROCESSING OF PIG-IRON, e.g. REFINING, MANUFACTURE OF WROUGHT-IRON OR STEEL; TREATMENT IN MOLTEN STATE OF FERROUS ALLOYS
    • C21C7/00—Treating molten ferrous alloys, e.g. steel, not covered by groups C21C1/00 - C21C5/00
    • C21C7/10—Handling in a vacuum
    • 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
    • C21D1/02—Hardening articles or materials formed by forging or rolling, with no further heating beyond that required for the formation
    • 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
    • C21D6/007—Heat treatment of ferrous alloys containing Co
    • 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
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • 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
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
    • 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
    • C21D8/06—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires
    • C21D8/065—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires 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
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • 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
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of 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
    • C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
    • 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
    • C21D2211/005—Ferrite
    • 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
    • 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
    • C21D2211/009—Pearlite

Definitions

  • the invention relates to the technical field of non-quenched and tempered steel, in particular to a high-strength and high-toughness non-quenched and tempered round steel and a preparation method thereof.
  • Non-quenched and tempered round steel is a medium-carbon low-alloy structural steel with comprehensive mechanical properties equivalent to the quenched and tempered heat treatment state in the hot-rolled state or normalized state or the air-cooled state after forging.
  • This steel type simplifies the production process and deforms and cracks more Less, thereby reducing energy consumption and production costs, so non-quenched and tempered steel has been valued by various countries, and has been rapidly developed and applied.
  • the existing non-quenched and tempered steel is mainly to increase the strength and toughness by adding a certain amount of alloying elements such as Cr, Ni or V.
  • the Chinese patent with the authorization announcement number CN104032214A discloses "a non-quenched and tempered steel is extremely "Production process”
  • the Chinese patent of CN106119711A discloses "non-quenched and tempered steel bar and its manufacturing method”
  • the invention uses a combination of strong and weak cooling through the water cooling method to reduce the temperature of the steel to achieve temperature controlled cooling, but temperature controlled rolling
  • the water-through cooling method is not adopted, which affects the production efficiency, and the impact energy of the produced bar is below 120J.
  • the present invention provides a high-strength and high-toughness non-quenched and tempered round steel, whose chemical composition and mass percentage are as follows: C: 0.27% to 0.33%, Si: 0.40% to 0.70%, Cr: 0.10% -0.30 %, Mn: 1.30% to 1.65%, S: 0.065% to 0.100%, Al: 0.005% to 0.040%, V: 0.06% to 0.020%, Ti: 0.010% to 0.040%, N: 0.0120% to 0.0250%, The balance is Fe and inevitable impurities.
  • the present invention breaks through the technical bottleneck of insufficient toughness of non-quenched and tempered steel, adds low-cost free-cutting element S, and obtains high-toughness non-quenched and tempered steel with excellent mechanical properties through process temperature controlled rolling and temperature controlled cooling after rolling Bar.
  • the chemical composition and mass percentage of a high-strength, high-toughness non-quenched and tempered round steel mentioned above are as follows: C: 0.30%, Si: 0.65%, Cr: 0.23%, Mn: 1.58%, S: 0.090%, Al: 0.010%, V: 0.13%, Ti: 0.025%, N: 0.0200%, manganese equivalent Mneq: 1.96%, the balance is Fe and inevitable impurities.
  • the chemical composition and mass percentage of a high-strength and high-toughness non-quenched and tempered round steel mentioned above are as follows: C: 0.31%, Si: 0.60%, Cr: 0.20%, Mn: 1.53%, S: 0.070%, Al: 0.015%, V: 0.14%, Ti: 0.020%, N: 0.0160%, manganese equivalent Mneq: 1.87%, the balance is Fe and inevitable impurities.
  • the chemical composition and mass percentage of a high-strength and high-toughness non-quenched and tempered round steel mentioned above are as follows: C: 0.32%, Si: 0.57%, Cr: 0.18%, Mn: 1.50%, S: 0.075%, Al: 0.008%, V: 0.12%, Ti: 0.015%, N: 0.0170%, manganese equivalent Mneq: 1.81%, the balance is Fe and inevitable impurities.
  • the chemical composition and mass percentage of a high-strength and high-toughness non-quenched and tempered round steel mentioned above are as follows: C: 0.33%, Si: 0.50%, Cr: 0.15%, Mn: 1.45%, S: 0.066%, Al: 0.011%, V: 0.09%, Ti: 0.015%, N: 0.0190%, manganese equivalent Mneq: 1.71%, the balance is Fe and inevitable impurities.
  • Another object of the present invention is to provide a method for preparing high-strength and high-toughness non-quenched and tempered round steel, characterized in that it includes the following steps: EAF smelting ⁇ LF refining ⁇ VD vacuum treatment ⁇ light reduction process continuous casting ⁇ slab cooling ⁇ Casting slab inspection ⁇ Continuous casting slab heating ⁇ Descaling ⁇ Opening under large pressure ⁇ Slow cooling into the pit ⁇ Intermediate billet heating ⁇ Descaling ⁇ Temperature controlled rolling ⁇ Controlled cooling ⁇ Straightening ⁇ Grinding ⁇ Flaw detection ⁇ Finished product inspection ⁇ Packaging ⁇ Identification ⁇ Weighing ⁇ Storage
  • the molten steel is guaranteed to have an Al content of ⁇ 0.025%, fully stirred with argon blowing throughout, to ensure that the white slag time is ⁇ 30 minutes, the process of blowing nitrogen for more than 35 minutes, and the Al content at the end of the LF is 0.030% ⁇ 0.040%, S content 0.065% ⁇ 0.090%, Si is controlled according to the middle and lower limit, and the rest is controlled according to the judged middle limit.
  • 0.5m / t ⁇ 1.5m / t Ca iron wire is fed to the inclusions.
  • the continuous casting machine of the large-section continuous casting machine gently presses down the continuous casting, the reduction is 8mm ⁇ 20mm, and the superheat is 15 °C ⁇ 30 °C;
  • the rolling open rolling temperature is above 950 °C, after rough and medium rolling, it is cooled by water, air cooling for 15-30 seconds, after pre-finishing rolling, it is again cooled by water, air cooling for 20-40 seconds, and the temperature of the finishing mill is 780 °C ⁇ 850 °C, the final rolling temperature is controlled at 800 °C ⁇ 850 °C, to achieve continuous cooling rolling.
  • the controlled cooling process after rolling, the water is quickly cooled, the temperature of the upper cooling bed is controlled below 700 ° C, the upper cooling bed controls the uniform spacing of the bars, and the cold bed is cooled below 400 ° C.
  • the molten steel is quickly fed by means of a wire feeder, which melts and dissolves deep in the molten steel, plays the role of deoxidation, desulfurization, and inclusion removal.
  • the composition can be fine-tuned to improve the element yield and ensure Ingredient stability;
  • the continuous casting machine with a large cross section is lightly pressed at the solidification end, and the superheat is 15-30 ° C to reduce segregation of components, especially to avoid segregation of sulfides;
  • water cooling is carried out after rough and medium rolling, and air cooling of the round steel is used for 15-30 seconds to promote the heat dissipation of the core to the surface, and the overall temperature is reduced. After pre-finishing rolling, water cooling is performed again, air cooling 20- 40 seconds to ensure that the surface temperature of the core of the hot-rolled round steel tends to be consistent and enter the finishing rolling stage;
  • the water is quickly cooled after rolling, the upper cooling bed controls the uniform spacing of the bars to achieve uniform low temperature phase transition, and the cold bed is cooled below 400 ° C. This process can obtain fine pearlite ferrite organization;
  • the bar of the present invention has a yield strength of 620 MPa or more, a tensile strength of 850 MPa or more, an elongation ⁇ 19%, and an impact energy of 190 J or more.
  • Example 1 0.27 1.65 0.70 0.010 0.085 0.25 0.15 0.030 0.013 0.0220 2.06
  • Example 2 0.30 1.58 0.65 0.012 0.090 0.23 0.13 0.025 0.010 0.0200 1.96
  • Example 3 0.31 1.53 0.60 0.008 0.070 0.20 0.14 0.020 0.015 0.0160 1.87
  • Example 4 0.32 1.50 0.57 0.013 0.075 0.18 0.12 0.015 0.008 0.0170 1.81
  • Example 5 0.33 1.45 0.50 0.011 0.066 0.15 0.09 0.015 0.011 0.0190 1.71
  • the preparation method includes the following steps: EAF smelting ⁇ LF refining ⁇ VD vacuum treatment ⁇ soft reduction process continuous casting ⁇ slow cooling of the casting slab ⁇ inspection of the casting slab ⁇ heating of the continuous casting slab ⁇ descaling ⁇ opening under large pressure ⁇ slow cooling into the pit ⁇ intermediate billet heating ⁇ descaling ⁇ temperature controlled rolling ⁇ controlled cooling ⁇ straightening ⁇ grinding ⁇ flaw detection ⁇ finished product inspection ⁇ packaging ⁇ identification ⁇ weighing ⁇ storage, the specific parameters are as follows:
  • the molten steel is guaranteed to have an Al content of ⁇ 0.025%, and the argon blowing is fully stirred during the whole process to ensure that the white slag time is ⁇ 30 minutes, the process of blowing nitrogen for more than 35 minutes, and the Al content at the end of the LF is 0.030% ⁇ 0.040%, S content 0.065% ⁇ 0.090%, Si is controlled according to the middle and lower limit, and the rest is controlled according to the determined middle limit.
  • 0.5m / t ⁇ 1.5m / t Ca iron wire is fed to modify the inclusions deal with;
  • the large-section continuous casting machine lightly reduces the continuous casting at the solidification end, the reduction is 8mm ⁇ 20mm, and the superheat is 15 ° C ⁇ 30 ° C, reducing component segregation, especially to avoid sulfide segregation;
  • Example 1-5 The bars of Example 1-5 were selected for low power, inclusion control level and mechanical property testing. The data obtained are shown in Table 2-4.
  • A sulfides
  • B alumina
  • C silicates
  • D spherical oxides
  • Hot rolled grain size 1 9.5 2 9.5 3 10 4 10 5 10.5
  • the present invention adopts the dispersion distribution of sulfide and V (N, C) fine compounds, V and Ti are slightly compounded, the rolling process uses staged water penetration, continuous uniform temperature reduction rolling, and water penetration after rolling
  • the controlled cooling process refines the structure and significantly improves the strength and impact toughness.
  • the impact energy of round steel can reach more than 190J, which is significantly higher than that of traditional non-quenched and tempered steel.
  • the present invention may have other embodiments. All technical solutions formed by equivalent replacement or equivalent transformation fall within the scope of protection required by the present invention.

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

Abstract

一种高强高韧性非调质圆钢，涉及非调质钢技术领域，其化学成分及质量百分比如下：C:0.27％～0.33％，Si:0.40％～0.70％，Cr:0.10％-0.30％，Mn:1.30％～1.65％，S:0.065％～0.100％，Al:0.005％～0.040％，V:0.06％～0.020％，Ti:0.010％～0.040％，N:0.0120％～0.0250％，余量为Fe和不可避免的杂质，锰当量Mneq:1.70％～2.10％。该非调质钢增加低成本的易切削元素S，形成硫化物、V(N、C)化合物弥散分布，通过过程连续均匀降温轧制和轧后的控温冷却，得到力学性能优良的高韧性非调质钢棒材，轧材冲击功达到190J以上。

Description

一种高强高韧性非调质圆钢及制备方法 技术领域
本发明涉及非调质钢技术领域，特别是涉及一种高强高韧性非调质圆钢及制备方法。
背景技术
非调质圆钢是在热轧状态或正火状态或锻造后空冷状态下具有与调质热处理态相当的综合力学性能的中碳低合金结构钢，该钢种简化了生产工艺，变形开裂较少，从而降低了能耗和生产成本，因此非调质钢受到各国的重视，得到迅速发展和应用。现有的非调质钢主要是通过添加一定量的合金元素如Cr、Ni或V等来提高强韧性，经检索发现，授权公告号为CN104032214A的中国专利公开了“一种非调质钢极其生产工艺”，CN106119711A的中国专利公开了“非调质钢棒材及其制造方法”，该发明采用强弱冷相结合的穿水冷却方式降低钢材温度，实现控温冷却，但是控温轧制未采用穿水冷却方式，影响生产效率，所生产棒材冲击功在120J以下。
发明内容
为了解决以上技术问题，本发明提供一种高强高韧性非调质圆钢，其化学成分及质量百分比如下：C:0.27％～0.33％，Si:0.40％～0.70％，Cr:0.10％-0.30％，Mn:1.30％～1.65％，S:0.065％～0.100％，Al:0.005％～0.040％，V:0.06％～0.020％，Ti:0.010％～0.040％，N:0.0120％～0.0250％，余量为Fe和不可避免的杂质，锰当量Mneq:1.70％～2.10％，Mneq＝％Mn+0.35％Ni+1.5％Cr+2％Mo+0.17％Cu。
技术效果：本发明突破非调质钢冲击韧性不足技术瓶颈，增加低成本的易切削元素S，通过过程控温轧制和轧后的控温冷却，得到力学性能优良的高韧性非调质钢棒材。
本发明进一步限定的技术方案是：
进一步的，其化学成分及质量百分比如下：C:0.27％，Si:0.70％，Cr:0.25％， Mn:1.65％，S:0.085％，Al:0.013％，V:0.15％，Ti:0.030％，N:0.0220％，锰当量Mneq：2.06％，余量为Fe和不可避免的杂质。
前所述的一种高强高韧性非调质圆钢，其化学成分及质量百分比如下：C:0.30％，Si:0.65％，Cr:0.23％，Mn:1.58％，S:0.090％，Al:0.010％，V:0.13％，Ti:0.025％，N:0.0200％，锰当量Mneq：1.96％，余量为Fe和不可避免的杂质。
前所述的一种高强高韧性非调质圆钢，其化学成分及质量百分比如下：C:0.31％，Si:0.60％，Cr:0.20％，Mn:1.53％，S:0.070％，Al:0.015％，V:0.14％，Ti:0.020％，N:0.0160％，锰当量Mneq：1.87％，余量为Fe和不可避免的杂质。
前所述的一种高强高韧性非调质圆钢，其化学成分及质量百分比如下：C:0.32％，Si:0.57％，Cr:0.18％，Mn:1.50％，S:0.075％，Al:0.008％，V:0.12％，Ti:0.015％，N:0.0170％，锰当量Mneq：1.81％，余量为Fe和不可避免的杂质。
前所述的一种高强高韧性非调质圆钢，其化学成分及质量百分比如下：C:0.33％，Si:0.50％，Cr:0.15％，Mn:1.45％，S:0.066％，Al:0.011％，V:0.09％，Ti:0.015％，N:0.0190％，锰当量Mneq：1.71％，余量为Fe和不可避免的杂质。
本发明的另一目的在于提供一种高强高韧性非调质圆钢制备方法，其特征在于，包括以下工序：EAF冶炼→LF精炼→VD真空处理→轻压下工艺连铸→铸坯缓冷→铸坯检验→连铸坯加热→除鳞→大压下开坯→入坑缓冷→中间坯加热→除鳞→控温轧制→控制冷却→矫直→修磨→探伤→成品检验→包装→标识→称重→入库，
EAF冶炼工序中：控制电炉终点碳≥0.06％，终点磷≤0.015％，出钢氧含量控制在300PPM以下，采用偏心炉底无渣出钢，出钢过程钢包内加合成渣、硅锰合金、复合中铝进行预脱氧，严禁出钢下渣；
LF精炼工序中：通过喂铝线和添加铝粒使钢水保证Al含量≥0.025％，全程吹氩充分搅拌，确保白渣时间≥30分钟，过程吹氮35分钟以上，LF末期Al含 量为0.030％～0.040％、S含量0.065％～0.090％，Si按照中下限控制，其余按照判定中限进行点成分控制，真空处理前喂入0.5m/t～1.5m/t的Ca铁线对夹杂物进行变性处理；
VD真空处理工序中：在VD工位前期吹氮，后切换到氩气搅拌，小于0.5乇的真空度下处理12～20分钟，微调Al、N、Ti含量，破真空后保证软吹时间15～20分钟；
大断面连铸机凝固末端轻压下连铸，压下量8mm～20mm，过热度15℃～30℃；
大压下开坯工序中：采用双辊可逆式轧机，最大辊径φ950，单道最大压下量达80mm；
控温轧制工序中：轧制开轧温度950℃以上，粗中轧后穿水冷却，空冷15～30秒，预精轧后再次穿水冷却，空冷20～40秒，进精轧机温度780℃～850℃，将终轧温度控制在800℃～850℃，实现连续降温轧制。
控制冷却工序中：轧制后穿水快速冷却,上冷床温度控制在700℃以下,上冷床控制棒材间距均匀冷却，400℃以下下冷床堆冷。
本发明的有益效果是：
(1)本发明中借助于喂丝机快速输入钢液，在钢液深处熔化溶解，起到脱氧、脱硫、去夹杂的作用，同时能对成分进行微调，能提高元素收得率，保证成份的稳定性；
(2)本发明中大断面连铸机凝固末端轻压下连铸，过热度15-30℃，减少成分偏析，特别是避免硫化物偏聚；
(3)本发明中粗中轧后穿水冷却，利用产线布局圆钢空冷15-30秒促使心部热量散到表面，实现整体温度降低，预精轧后再次穿水冷却，空冷20-40秒，保证热轧圆钢心部表面温度趋于一致后进入精轧阶段；
(4)本发明中轧制后穿水快速冷却，上冷床控制棒材间距均匀冷却、实现均匀低温相变，400℃以下下冷床堆冷，此工艺可以得到细小的珠光体铁素体组织；
(5)本发明棒材屈服强度620MPa以上，抗拉强度850MPa以上，延伸率≥19％，冲击功可达到190J以上。
具体实施方式
本实施例提供的一种高强高韧性非调质圆钢，其化学成分及质量百分比如下：C:0.27％～0.33％，Si:0.40％～0.70％，Cr:0.10％-0.30％，Mn:1.30％～1.65％，S:0.065％～0.100％，Al:0.005％～0.040％，V:0.06％～0.020％，Ti:0.010％～0.040％，N:0.0120％～0.0250％，余量为Fe和不可避免的杂质，锰当量Mneq:1.70％～2.10％，Mneq＝％Mn+0.35％Ni+1.5％Cr+2％Mo+0.17％Cu。
根据本发明的生产工艺，冶炼轧制本发明的钢种各实施例成分如表1所示。
表1：实施例1-5的化学成分(wt％)
编号 C Mn Si P S Cr V Ti Al N Mneq
实施例1 0.27 1.65 0.70 0.010 0.085 0.25 0.15 0.030 0.013 0.0220 2.06
实施例2 0.30 1.58 0.65 0.012 0.090 0.23 0.13 0.025 0.010 0.0200 1.96
实施例3 0.31 1.53 0.60 0.008 0.070 0.20 0.14 0.020 0.015 0.0160 1.87
实施例4 0.32 1.50 0.57 0.013 0.075 0.18 0.12 0.015 0.008 0.0170 1.81
实施例5 0.33 1.45 0.50 0.011 0.066 0.15 0.09 0.015 0.011 0.0190 1.71
制备方法包括以下工序：EAF冶炼→LF精炼→VD真空处理→轻压下工艺连铸→铸坯缓冷→铸坯检验→连铸坯加热→除鳞→大压下开坯→入坑缓冷→中间坯加热→除鳞→控温轧制→控制冷却→矫直→修磨→探伤→成品检验→包装→标识→称重→入库，具体参数如下：
EAF冶炼工序中：控制电炉终点碳≥0.06％，终点磷≤0.015％，出钢氧含量控制在300PPM以下，采用偏心炉底无渣出钢，出钢过程钢包内加合成渣、硅锰 合金、复合中铝进行预脱氧，严禁出钢下渣；
LF精炼工序中：通过喂铝线和添加铝粒使钢水保证Al含量≥0.025％，全程吹氩充分搅拌，确保白渣时间≥30分钟，过程吹氮35分钟以上，LF末期Al含量0.030％～0.040％、S含量0.065％～0.090％，Si按照中下限控制，其余按照判定中限进行点成分控制，真空处理前喂入0.5m/t～1.5m/t的Ca铁线对夹杂物进行变性处理；
VD真空处理工序中：在VD工位前期吹氮，后切换到氩气搅拌，小于0.5乇的真空度下处理12～20分钟，微调Al、N、Ti含量，破真空后保证软吹时间15～20分钟；
连铸工序中：大断面连铸机凝固末端轻压下连铸，压下量8mm～20mm，过热度15℃～30℃，减少成分偏析，特别是避免硫化物偏聚；
大压下开坯工序中：采用双辊可逆式轧机，最大辊径φ950，单道最大压下量达80mm；
轧后控冷工序中：粗中轧后穿水冷却、利用产线布局圆钢空冷15～30秒促使心部热量散到表面，实现整体温度降低，预精轧后再次穿水冷却，空冷20～40秒，保证热轧圆钢心部表面温度趋于一致后进入精轧阶段，进精轧机温度780℃～850℃，将终轧温度控制在800℃～850℃，实现连续降温轧制。
控制冷却工序中：轧制后穿水快速冷却,上冷床温度控制在700℃以下,上冷床控制棒材间距均匀冷却、实现均匀低温相变，400℃以下下冷床堆冷，此工艺可以得到细小的珠光体铁素体组织。
选取实施例1-5的棒材进行低倍、夹杂物控制级别及力学性能检测，所得数据如表2-4所示。
表2：实施例1-5棒材低倍检测所得数据
实施例 一般疏松 中心疏松 锭型偏析
1 0.5 1.0 0.5
2 0.5 1.0 0
3 0.5 1.0 0.5
4 0.5 1.5 0.5
5 0 1.0 0.5
表3：实施例1-5棒材中夹杂物控制级别显微检测所得数据
Figure PCTCN2019089346-appb-000001
表中A，硫化物类；B，氧化铝类；C，硅酸盐类；D，球状氧化物类；
表4：实施例1-5棒材力学性能检测所得数据
Figure PCTCN2019089346-appb-000002
表中Rm，抗拉强度；Rp0.2，屈服强度；Aku，冲击吸收功；A，断后延伸率；
表5：实施例1-5棒材晶粒度检测所得数据
实施例 热轧态晶粒度
1 9.5
2 9.5
3 10
4 10
5 10.5
由表2-5可知，本发明棒材在下游客户加工成轮毂、控制臂、后摆臂等， 用于装于乘用车，测试表明各项性能良好，完全满足使用要求。
综上所述，本发明采用硫化物、V(N、C)细小化合物的弥散分布，V、Ti微量复合，轧制过程中采用分段穿水、连续均匀降温轧制、轧后穿水的控冷工艺，细化组织、显著提高了强度及冲击韧性，圆钢冲击功可达到190J以上，明显高于传统非调质钢。
除上述实施例外，本发明还可以有其他实施方式。凡采用等同替换或等效变换形成的技术方案，均落在本发明要求的保护范围。

Claims (7)

  1. 一种高强高韧性非调质圆钢，其特征在于，其化学成分及质量百分比如下：C:0.27％～0.33％，Si:0.40％～0.70％，Cr:0.10％-0.30％，Mn:1.30％～1.65％，S:0.065％～0.100％，Al:0.005％～0.040％，V:0.06％～0.020％，Ti:0.010％～0.040％，N:0.0120％～0.0250％，余量为Fe和不可避免的杂质，锰当量Mneq:1.70％～2.10％，Mneq＝％Mn+0.35％Ni+1.5％Cr+2％Mo+0.17％Cu。
  2. 根据权利要求1所述的一种高强高韧性非调质圆钢，其特征在于，其化学成分及质量百分比如下：C:0.27％，Si:0.70％，Cr:0.25％，Mn:1.65％，S:0.085％，Al:0.013％，V:0.15％，Ti:0.030％，N:0.0220％，锰当量Mneq：2.06％，余量为Fe和不可避免的杂质。
  3. 根据权利要求1所述的一种高强高韧性非调质圆钢，其特征在于，其化学成分及质量百分比如下：C:0.30％，Si:0.65％，Cr:0.23％，Mn:1.58％，S:0.090％，Al:0.010％，V:0.13％，Ti:0.025％，N:0.0200％，锰当量Mneq：1.96％，余量为Fe和不可避免的杂质。
  4. 根据权利要求1所述的一种高强高韧性非调质圆钢，其特征在于，其化学成分及质量百分比如下：C:0.31％，Si:0.60％，Cr:0.20％，Mn:1.53％，S:0.070％，Al:0.015％，V:0.14％，Ti:0.020％，N:0.0160％，锰当量Mneq：1.87％，余量为Fe和不可避免的杂质。
  5. 根据权利要求1所述的一种高强高韧性非调质圆钢，其特征在于，其化学成分及质量百分比如下：C:0.32％，Si:0.57％，Cr:0.18％，Mn:1.50％，S:0.075％，Al:0.008％，V:0.12％，Ti:0.015％，N:0.0170％，锰当量Mneq：1.81％，余量为Fe和不可避免的杂质。
  6. 根据权利要求1所述的一种高强高韧性非调质圆钢，其特征在于，其化学成分及质量百分比如下：C:0.33％，Si:0.50％，Cr:0.15％，Mn:1.45％，S:0.066％，Al:0.011％，V:0.09％，Ti:0.015％，N:0.0190％，锰当量Mneq：1.71％，余量为Fe和不可避免的杂质。
  7. 一种高强高韧性非调质圆钢制备方法，其特征在于，包括以下工序：EAF冶炼→LF精炼→VD真空处理→轻压下工艺连铸→铸坯缓冷→铸坯检验→连铸坯加热→除鳞→大压下开坯→入坑缓冷→中间坯加热→除鳞→控温轧制→控制冷却→矫直→修磨→探伤→成品检验→包装→标识→称重→入库，
    EAF冶炼工序中：控制电炉终点碳≥0.06％，终点磷≤0.015％，出钢氧含量控制在300PPM以下，采用偏心炉底无渣出钢，出钢过程钢包内加合成渣、硅锰合金、复合中铝进行预脱氧，严禁出钢下渣；
    LF精炼工序中：通过喂铝线和添加铝粒使钢水保证Al含量≥0.025％，全程吹氩充分搅拌，确保白渣时间≥30分钟，过程吹氮35分钟以上，LF末期Al含量为0.030％～0.040％、S含量0.065％～0.090％，Si按照中下限控制，其余按照判定中限进行点成分控制，真空处理前喂入0.5m/t～1.5m/t的Ca铁线对夹杂物进行变性处理；
    VD真空处理工序中：在VD工位前期吹氮，后切换到氩气搅拌，小于0.5乇的真空度下处理12～20分钟，微调Al、N、Ti含量，破真空后保证软吹时间15～20分钟；
    大断面连铸机凝固末端轻压下连铸，压下量8mm～20mm，过热度15℃～30℃；
    大压下开坯工序中：采用双辊可逆式轧机，最大辊径φ950，单道最大压下量达80mm；
    控温轧制工序中：轧制开轧温度950℃以上，粗中轧后穿水冷却，空冷15～30秒，预精轧后再次穿水冷却，空冷20～40秒，进精轧机温度780℃～850℃，将终轧温度控制在800℃～850℃，实现连续降温轧制。
    控制冷却工序中：轧制后穿水快速冷却,上冷床温度控制在700℃以下,上冷床控制棒材间距均匀冷却，400℃以下下冷床堆冷。
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