WO2014114041A1 - 一种780MPa级冷轧双相带钢及其制造方法 - Google Patents

一种780MPa级冷轧双相带钢及其制造方法 Download PDF

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WO2014114041A1
WO2014114041A1 PCT/CN2013/076184 CN2013076184W WO2014114041A1 WO 2014114041 A1 WO2014114041 A1 WO 2014114041A1 CN 2013076184 W CN2013076184 W CN 2013076184W WO 2014114041 A1 WO2014114041 A1 WO 2014114041A1
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cold
steel
rolled
manufacturing
mpa grade
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French (fr)
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朱晓东
李旭飞
杜培芳
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Baoshan Iron and Steel Co Ltd
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Baoshan Iron and Steel Co Ltd
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Priority to EP13872680.7A priority Critical patent/EP2949774B1/en
Priority to ES13872680.7T priority patent/ES2685593T3/es
Priority to MX2015009431A priority patent/MX370969B/es
Priority to CA2897885A priority patent/CA2897885C/en
Priority to JP2015552973A priority patent/JP6285462B2/ja
Priority to US14/761,473 priority patent/US11377711B2/en
Priority to KR1020157022817A priority patent/KR20150110723A/ko
Publication of WO2014114041A1 publication Critical patent/WO2014114041A1/zh
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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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/52—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length
    • 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
    • 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties of ferrous metals or ferrous alloys 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0236—Cold rolling
    • 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
    • C22C38/06—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
    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
    • 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
    • C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
    • 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
    • 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

Definitions

  • the present invention relates to a duplex steel and a method of manufacturing the same, and more particularly to an iron-based dual phase steel and a method of manufacturing the same. Background technique
  • the dual-phase strip steel with tensile strength of 780 MPa has good strength and formability, so it has a good application prospect.
  • the 780Mpa dual-phase strip is expected to replace the market position of 590MPa cold-rolled dual-phase steel in the future and become the most widely used duplex steel.
  • Duplex steel is made by strengthening the phase transformation. In order to ensure a certain hardenability, certain carbon and alloying elements must be added to the steel to ensure that the super-cooled austenite can be transformed into a horse during the cooling process. Clan.
  • the carbon equivalent of steel mainly depends on the carbon content in the steel, the content of alloying elements and the content of impurity elements.
  • Pcm C + Si / 30 + Mn / 20 + 2P + 4S.
  • the Pcm value can be used to characterize the brittleness tendency of steel plates after cooling. When the Pcm is higher than 0.24, the interface crack of the solder joint is liable to occur; when the Pcm is lower than 0.24, it is safe.
  • Steel is essentially an anisotropic material. Since the strip production is continuous production, the steel structure has a directionality of distribution to varying degrees, that is, an elongated strip-like distribution along the rolling direction. In high-strength steel, since the alloying elements are high, composition segregation is very likely to occur, and segregation of the substitutional alloying elements is difficult to eliminate, and is deformed and elongated in the hot rolling and cold rolling processes to finally form a band structure. Generally, the band structure contains high alloying elements and carbon content, which causes the duplex steel to form a hard and brittle martensite which exhibits a band-like distribution after quenching, which is harmful to the performance of the steel.
  • the publication number is CN102212745A, and the publication date is October 12, 2011.
  • the Chinese patent document entitled "A high plasticity 780MPa grade cold rolled dual phase steel and its preparation method" discloses a high plasticity 780MPa cold rolled duplex steel.
  • the chemical composition of the method is: 0.06 ⁇ 0.08%C, 1.0 ⁇ 1.3%Si, 2 ⁇ b 2 ⁇ 3% ⁇ , 0 ⁇ 02 ⁇ 0 ⁇ 07 % ⁇ 1, S ⁇ O.01%, N ⁇ O .005 %, P ⁇ O.01%, the balance is Fe and other unavoidable impurities.
  • the hot rolling finishing temperature is 890 ° C, the coiling temperature is 670 ° C, and the cold rolling reduction is 50-70%; continuous annealing is performed by conventional jet cooling.
  • the rapid cooling rate is 1001 ⁇ , and the rapid cooling termination temperature is lower than 300°.
  • C finally obtained cold-rolled high-strength steel having a tensile strength of 780 MPa or more and a hole expansion ratio of at least 60%.
  • the composition of the steel plate is designed to have a high Mn content and a high Si content.
  • Japanese patent document entitled "High-strength cold-rolled steel sheet with small change in mechanical properties and its manufacturing method” is disclosed in Japanese Patent Publication No. 2007-138262, the disclosure of which is incorporated herein by reference.
  • its chemical composition is: 0.06 ⁇ 0.15%C, 0.5 ⁇ 1.5%Si, 1.5 ⁇ 3.0%Mn, 0.5 ⁇ 1.5%A1, S ⁇ O.01%, P ⁇ O.05%, balance is Fe and others Inevitable impurities.
  • the manufacturing process is as follows: Acl ⁇ Ac3 is kept for 10 s, cooled to 500 ⁇ 750 ° C at a cooling rate of 20 ° C / s, and cooled to below 100 ° C at a cooling rate of 100 ° C /s or more to obtain 780 MPa and a hole expansion ratio. 60 high strength steel plate.
  • the object of the present invention is to provide a 780 MPa grade cold-rolled double-phase strip steel and a manufacturing method thereof.
  • the cold-rolled double-phase strip steel is designed by a low carbon equivalent, and it is desired to obtain uniform microstructure, good phosphating performance and anisotropy of mechanical properties.
  • the smaller duplex steel strips are able to meet the two-way requirements of the automotive industry for thinner and stronger steels.
  • the present invention provides a 780 MPa grade cold-rolled duplex steel strip having a microstructure of a fine equiaxed ferrite matrix and a martensite island uniformly distributed on the ferrite matrix, and Its chemical element mass percentage is:
  • At least one of Nb and Ti elements, and Nb+Ti is in the range of 0.02 to 0.05%;
  • the balance is Fe and other unavoidable impurities.
  • C The design principle of each chemical element in the 780MPa grade cold-rolled dual-phase strip steel according to the present invention is as follows: C: C can increase the strength of martensite and affect the content of martensite. It has a great influence on the strength, but the increase in carbon content is detrimental to the weldability of the strip. When the carbon content is less than 0.06 %, the strength is not sufficient; when the carbon content is higher than 0.1%, the weldability is lowered. Therefore, the technical solution of the present invention selects a carbon content of between 0.06 and 0.1 wt%.
  • Si acts as a solid solution strengthening in duplex steel. Si can increase the activity of carbon, promote the segregation of C in the Mn-rich region, and increase the carbon content of the band. However, Si does not favor the phosphating performance of the steel strip, so it is necessary to control the upper limit of the Si content.
  • the technical solution described in the present invention requires Si 0.28 wt%.
  • Mn can improve the hardenability of steel and effectively increase the strength of steel, but Mn is not conducive to the welding performance of steel strip. Mn segregates in steel and is easily rolled into a band-shaped Mn-rich region during hot rolling to form a band-like structure, which is not conducive to the uniformity of the microstructure of the duplex steel. When Mn is less than 1.8%, the hardenability of the strip is insufficient and the strength is insufficient; when Mn is higher than 2.3%, the band structure in the strip is intensified and the carbon equivalent is increased. Therefore, the content of Mn is set to 1.8 to 2.3% by weight.
  • Cr can improve the hardenability of the strip, and the addition of Cr can supplement the effect of Mn.
  • the Cr content is controlled to be 0.1 to 0.4% by weight.
  • Mo can improve the hardenability of steel, effectively increase the strength of the strip, and Mo can improve the carbide distribution. Mo and Cr together play an auxiliary role in the hardenability of the strip, Therefore, in the technical solution, the amount of Mo added is related to Cr. When the Cr content is less than 0.3% by weight, the amount of Mo added should satisfy (0.3-Cr); when the Cr content is higher than 0.3% by weight, it is not required. Add Mo.
  • Al acts as a deoxidation and grain refinement in steel.
  • Al is required to be 0.015 to 0.05 wt%.
  • Nb, Ti: Nb and Ti are precipitation strengthening elements, which can refine grains. They can be added separately or in combination, but the total addition should be controlled at 0.02 ⁇ 0.05wt%.
  • the 780 MPa grade cold-rolled duplex steel strip of the present invention is defined by the following chemical elements, wherein: C 0.07 to 0.09 wt%; Mn 1.9 to 2.2 wt%; Al 0.02 to 0.04 wt%.
  • the 780 MPa grade cold-rolled duplex steel strip of the present invention employs a lower carbon content, a lower total amount of alloying elements added, and a composite addition of various alloying elements.
  • selecting a lower carbon content can reduce the enrichment degree of C in the steel and reduce the tendency of the band structure; and selecting to reduce the content of the main alloying element Mn in the dual-phase steel can effectively reduce the strip steel.
  • the probability of occurrence of banded structure and the adverse effect on phosphating performance are strictly limited, the addition of Si is strictly limited, and the segregation of C atoms due to the change of C atom activity by Si is reduced; a certain amount of other alloying elements such as Cr and Mo are added.
  • Such a component design can effectively control the carbon equivalent Pcm in the steel to be less than 0.24, and not only can obtain a welded cross-stretch button-shaped fracture, but also ensure that the strip strength is not lower than 780 MPa. Since the microstructure of the phase strip is a small equiaxed ferrite matrix and a martensite island uniformly distributed on the ferrite matrix, the banded structure is slightly present, so the mechanical properties of the strip are It has a small anisotropy and good cold bending and hole expanding properties.
  • the present invention also provides a method of manufacturing the 780 MPa grade cold rolled duplex steel strip, which comprises the following steps:
  • Hot rolling control the final rolling temperature to 820 ⁇ 900 °C, and quickly cool after rolling;
  • Winding Control the coiling temperature 450 ⁇ 650 °C;
  • the step 7) is further included.
  • the cold rolling reduction ratio is 40 to 60%.
  • the flattening ratio is 0.1 to 0.4%.
  • the two cold water process is adopted in the continuous casting step, and the rapid cooling of the steel slab with rapid cooling rate and large cooling water spray can refine the slab structure, so that the fine carbide is granules. Disperse distribution in the ferrite matrix.
  • a lower finish rolling temperature is employed in the hot rolling process, and a lower coiling temperature is also employed in the coiling step, which can refine the grains while reducing the distribution continuity of the banded structure.
  • the use of a higher annealing temperature in the continuous annealing step can inhibit the formation of banded structure in the steel, and rapid cooling after uniform heating, which is also beneficial to reduce the segregation of carbon and the formation of banded structure.
  • the microstructure of the 780 MPa grade cold-rolled duplex steel strip of the present invention is a fine equiaxed ferrite matrix and a martensite island uniformly distributed on the ferrite matrix.
  • the anisotropy of mechanical properties is small and the structure is uniform.
  • the 780MPa grade cold-rolled double-phase strip steel of the invention has uniform martensite distribution, slight band structure, fine and compact surface phosphating film, good weldability and excellent mechanical properties. Sex, high-quality phosphating performance, small difference in longitudinal and transverse properties, is conducive to the stamping of duplex steel, can meet the requirements of strength and forming of high-strength dual-phase steel, and can be widely used in automotive manufacturing and other fields.
  • the method for manufacturing the 780 MPa grade cold-rolled double-phase strip steel according to the present invention can obtain uniform microstructure and good cold by reasonable composition design and improved manufacturing steps without increasing the difficulty of any process. Bending and reaming properties, high strength cold rolled duplex steel with low mechanical properties. DRAWINGS
  • Fig. 1 shows the microstructure of the cast state of the 780 MPa grade cold rolled duplex steel strip as referred to in Example 3.
  • Fig. 2 shows the microstructure of the 780 MPa grade cold rolled duplex steel strip involved in Example 3. detailed description
  • the technical solution of the present invention will be further described based on the specific embodiments and the drawings.
  • the 780 MPa grade cold rolled duplex steel strip of the present invention was produced according to the following procedure:
  • Hot rolling control the final rolling temperature to 820 ⁇ 900 °C, and quickly cool after rolling;
  • Winding Control the coiling temperature 450 ⁇ 650 °C;
  • cold rolling, cold rolling reduction rate is 40 ⁇ 60%
  • Table 2 shows the specific process parameters for each example.
  • the distribution ratio of the embodiment 2 shown in Table 1 is used, and the embodiment 5-1 and the embodiment 5-2 are both shown in the embodiment 5 shown in Table 1. Into the distribution ratio.
  • Table 3 shows the properties of the cold rolled duplex steels involved in various embodiments of the present technical solution.
  • the 780 MPa grade cold-rolled dual-phase strip steel of the present invention has high strength, good elongation, relatively small anisotropy of mechanical properties, and can replace 590 MPa cold-rolled dual-phase steel. Used in the field of automobile manufacturing.
  • Fig. 1 shows the as-cast microstructure of the embodiment 3 of the present invention
  • Fig. 2 shows the microstructure of the embodiment of the present invention.
  • the as-cast microstructure of the cold-rolled duplex steel is a cementite dispersed on the ferrite grains.
  • the microstructure of the cold rolled duplex steel strip is a fine equiaxed ferrite matrix and a martensite island uniformly distributed on the ferrite matrix, and the banded structure is slight.

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  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
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Abstract

一种780MPa级冷轧双相带钢，其微观组织为细小的等轴状铁素体基体以及在铁素体基体上均匀分布的马氏体岛，且其化学元素质量百分含量为：C:0.06∼0.1%；Si≤0.28%；Mn:1.8∼2.3%；Cr:0.1∼0.4%；Mo： Cr≥0.3%时，不添加；Cr＜0.3%时，Mo=0.3-Cr；Al：0.015∼0.05%；Nb、 Ti元素中的至少一种，且Nb+Ti在0.02∼0.05%范围内；余量为Fe和其他不可避免的杂质。相应地，还提供了该780MPa级冷轧双相带钢的制造方法。该780MPa级冷轧双相带钢具有较高的强度，良好的延展率，较好的磷化性，力学性能各向异性较小。

Description

一种 780MPa级冷轧双相带钢及其制造方法
技术领域
本发明涉及一种双相钢及其制造方法， 尤其涉及一种铁基双相钢及其制 造方法。 背景技术
随着汽车工业出于减重和安全性的需要， 市场对厚度更薄和强度更高的 钢板的需求量越来越多。 其中， 抗拉强度为 780Mpa的双相带钢的强度和成 形性兼顾性能较好， 因此具备较好的应用前景。 780Mpa 的双相带钢有望在 未来取代 590MPa的冷轧双相钢的市场地位， 成为应用最为广泛的双相钢。 双相钢是通过相变进行强化而制成的， 为了保证一定的淬硬性， 钢中必须加 入一定的碳和合金元素， 以确保双相钢在冷却过程中过冷奥氏体能够转变成 马氏体。 但是较高的碳元素含量和合金元素含量不利于钢板的焊接性， 而且 在铸造过程中合金元素容易发生成分偏析， 导致冷轧带钢中出现带状组织。 最终， 冷轧双相钢在不同方向上存在较大差异， 造成实际使用过程中一系列 的问题。
钢的碳当量主要取决于钢中的含碳量、 合金元素含量和杂质元素的含 量。碳当量的表征有许多不同的表达式，在汽车用钢中常用 Pcm值来表示， Pcm=C+Si/30+Mn/20+2P+4S。 一般说来， Pcm值可以用来表征钢板焊接冷 却后的脆性倾向。 当 Pcm高于 0.24时， 容易发生焊点的界面开裂； 当 Pcm 低于 0.24时， 则是安全的。
钢材本质是一种各向异性的材料。 由于带钢生产都采用连续生产， 因此 钢材组织不同程度地存在分布上的方向性， 即沿轧制方向呈现拉长的带状分 布。 高强度钢中由于合金元素较高， 非常容易发生成分偏析， 并且置换型合 金元素的偏析难以消除， 在热轧和冷轧过程中被变形拉长， 最终形成带状组 织。 通常， 带状组织含有高的合金元素和含碳量， 造成双相钢在淬火后形成 呈现带状分布的又硬又脆的马氏体， 对钢材性能的危害较大。 所以， 对于高 强度的双相带钢而言， 减轻带状组织以获得均匀分布的组织是获得优良性能 的关键。 公开号为 CN102212745A, 公开日为 2011年 10月 12日， 名称为 "一种 高塑性 780MPa级冷轧双相钢及其制备方法" 的中国专利文献公开了一种高 塑性 780MPa冷轧双相钢的制造方法， 其化学成分为： 0.06〜0.08%C， 1.0〜 1.3%Si, 2·卜 2·3%Μη， 0·02〜0·07 %Α1， S^O.01%, N^O.005 %, P^O.01%, 余量为 Fe和其他不可避免杂质。热轧终轧温度为 890 °C，卷取温度为 670 °C， 冷轧压下量为 50-70%; 采用常规的喷气冷却连续退火。
公开号为 US20040238082A1 , 公开日为 2004年 12月 2日， 名称为 "高 强度冷轧钢板及其制造方法"的美国专利文献介绍了一种扩孔性好的高强钢 的制造方法， 其化学成分为： 0.04〜0.1%C， 0.5〜1.5%Si， 1.8〜3%Mn， P 0.020%， S^O.01%, 0.01〜0.1%A1， N^O.005%, 余量为 Fe和其他不可避 免杂质。该钢板在 Ar3〜870°C之间热轧， 620°C以下卷取， 750〜870°C退火， 550〜750°C开始快冷， 快冷速率 1001^， 快冷终止温度低于 300°C， 最终 获得抗拉强度在 780Mpa以上且扩孔率至少为 60%的冷轧高强钢。该钢板的 成分设计采用了较高的 Mn含量和较多的 Si含量。
公开号为 JP特开 2007-138262， 公开日为 2007年 6月 7日， 名称为 "机 械性能变化小的高强度冷轧钢板及其制造方法" 的日本专利文献涉及一种高 强度冷轧钢板， 其化学成分为： 0.06〜0.15%C， 0.5〜1.5%Si， 1.5〜3.0%Mn， 0.5〜1.5 %A1， S^O.01%, P^O.05%, 余量为 Fe和其他不可避免杂质。 制造 工艺为： Acl〜Ac3保持 10s，以 20°C/s冷却速度冷却到 500〜750°C，以 100 °C /s以上的冷却速度冷却到 100°C以下， 可以获得 780MPa且扩孔率 60高强 度钢板。
上述专利文献均未对钢中带状组织的控制进行描述， 也没有针对各向异 性的改善提供相应的解决方法， 因此上述专利并未涉及有关双相钢各向力学 性能差异性的改善。 发明内容
本发明的目的在于提供一种 780MPa级冷轧双相带钢及其制造方法， 该 冷轧双相带钢通过低碳当量设计， 希望获得微观组织均匀， 磷化性能良好且 力学性能各向异性较小的双相带钢， 从而能够满足汽车工业领域对于钢材料 厚度更薄且强度更高的双向要求。 为达到上述发明目的， 本发明提供了一种 780MPa级冷轧双相带钢， 其 微观组织为细小的等轴状铁素体基体以及在铁素体基体上均匀分布的马氏体 岛， 且其化学元素质量百分含量为：
C 0.06—0.1%；
Si <0.28%；
Mn 1.8—2.3%；
Cr 0·卜 0.4%;
Mo Cr≥0.3%时， 不添加； Cr<0.3%时， Mo=0.3-Cr;
A1 0·015〜0·05%;
Nb、 Ti元素中的至少一种， 且 Nb+Ti在 0.02〜0.05%范围内；
余量为 Fe和其他不可避免的杂质。
本发明所述的 780MPa级冷轧双相带钢中的各化学元素的设计原理为： C: C可以提高马氏体的强度， 并影响马氏体的含量。 其对强度影响很 大， 但是含碳量的提高对带钢焊接性不利。 当含碳量低于 0.06 %， 强度不 够； 当含碳量高于 0.1 %， 焊接性下降。 因此， 本发明所述的技术方案选择 含碳量在 0.06〜0.1wt%之间。
Si: Si在双相钢钢中起到固溶强化的作用。 Si能够提高碳元素的活度， 可促进 C在富 Mn区的偏聚， 增加带状区域的含碳量。但是， Si对带钢的磷 化性能不利， 故需要对 Si含量的上限进行控制， 本发明所述的技术方案要 求 Si 0.28wt%。
Mn: Mn可提高钢的淬透性， 有效地提高钢的强度， 但 Mn不利于带 钢的焊接性能。 Mn在钢中偏析， 在热轧过程中容易被轧制成带状分布的 Mn富集区，形成带状组织，不利于双相钢的组织均匀性。当 Mn低于 1.8% 时， 带钢的淬透性不足， 强度不够； 当 Mn高于 2.3%时， 带钢中的带状组 织加剧， 碳当量增高。 因此， 将 Mn的含量设定为 1.8〜2.3wt%。
Cr: Cr可提高带钢的淬透性， 同时添加 Cr可以补充 Mn的作用。 当 Cr 低于 0.1%时， 作用不明显， 但是当 Cr高于 0.4%时， 会造成强度偏高， 塑性 下降。 所以， 本发明所述的技术方案中将 Cr含量控制为 0.1〜0.4wt%。
Mo: Mo可提高钢的淬透性， 有效地提高带钢的强度， Mo 能对碳化 物分布起到改善作用。 Mo和 Cr共同对带钢的淬透性能起到辅助作用， 因 此， 本技术方案中， Mo的添加量和 Cr有关， 当 Cr含量低于 0.3wt%时， Mo的添加量应满足 （0.3-Cr) ； 当 Cr含量高于 0.3wt%时， 则不需要添加 Mo。
Al: A1在钢中起到了脱氧作用和细化晶粒的作用。 本发明的技术方案 中要求 Al: 0.015〜0.05 wt%。
Nb、 Ti: Nb和 Ti为析出强化元素， 能起到细化晶粒的作用， 可以单独 添加或复合添加， 但是总添加量应控制在 0.02~0.05wt%。
进一歩地， 本发明所述的 780MPa级冷轧双相带钢对于下述化学元素作 出限定， 其中： C 0.07〜0.09wt%； Mn 1.9〜2.2wt%； Al 0.02〜0.04wt%。
在成分设计方面， 本发明所述的 780MPa级冷轧双相带钢采用了较低的 含碳量， 较低的合金元素添加总量和多种合金元素复合添加的方式。 对于本 技术方案来说， 选择较低的含碳量， 可以降低 C在钢中的富集程度， 减少带 状组织倾向；选择降低双相钢中主要合金元素 Mn的含量，可以有效降低带钢 出现带状组织的几率及减少对磷化性能的不良影响， 严格限制 Si的添加， 减 少由于 Si改变 C原子活度而引起的 C原子偏聚； 添加一定量的 Cr、 Mo等 其它合金元素含量， 可以弥补 Mn含量较低而造成的淬透性下降。 这样的成 分设计可以有效地控制钢中的碳当量 Pcm低于 0.24，不仅可以获得焊接十字 拉伸纽扣状断裂， 还可以保证带钢强度不低于 780MPa。 由于该相带钢的微 观组织为细小的等轴状铁素体基体以及在铁素体基体上均匀分布的马氏体 岛， 其所呈现的带状组织轻微， 所以带钢的力学性能的各向异性较小， 具有 良好的冷弯和扩孔性能。
相应地， 本发明还提供了该 780MPa级冷轧双相带钢的制造方法， 其包 括下列歩骤：
1) 冶炼；
2) 铸造： 采用二冷水工艺， 喷水量不低于 0.7L水 /每公斤钢坯；
3) 热轧： 控制终轧温度为 820〜900°C， 轧后快速冷却；
4) 卷取： 控制卷取温度 450〜650°C ;
5) 冷轧；
6) 连续退火： 800〜860°C保温，以不小于 5 °C/s的冷速冷却到 640〜700°C 之间，再以 40〜100°C/s速度冷却到 220〜280°C之间，在 220〜280°C 之间回火 100〜300s。
进一歩地， 在上述 780MPa级冷轧双相带钢的制造方法中， 还包括歩骤 7) 平整。
进一歩地， 在上述歩骤 （5 ) 中， 冷轧压下率为 40〜60%。
更进一歩地， 在上述歩骤 7 ) 中， 平整率为 0.1〜0.4%。
在制造工艺方面， 在连铸歩骤中采用二冷水工艺， 以较快的冷却速度和 较大的冷却喷水量快速均匀冷却钢坯可以细化连铸坯组织， 这样， 细小的碳 化物呈颗粒状弥散分布于铁素体基体。在热轧歩骤中采用了较低的终轧温度， 且卷取歩骤中也采用了较低的卷取温度， 这样可以细化晶粒， 同时降低带状 组织的分布连续性。 在连续退火歩骤中采用了较高的退火保温温度， 可以抑 制钢中带状组织的形成， 均匀加热后快速冷却， 也有利于减轻碳的偏聚和带 状组织的形成。 经过上述工艺歩骤后， 本发明所述的 780MPa级冷轧双相带 钢的微观组织呈现为细小的等轴状铁素体基体以及在铁素体基体上均匀分布 的马氏体岛， 其力学性能的各向异性小， 并且组织结构均匀。
与现有技术相比， 本发明所述的 780MPa级冷轧双相带钢， 马氏体分布 均匀， 带状组织轻微， 表面磷化膜细小致密； 具有良好的焊接性， 优良的力 学性能均匀性， 优质的磷化性能， 纵向和横向性能差异小， 有利于双相钢的 冲压成形， 能够满足对高强度双相钢在强度和成形方面的要求， 能够广泛应 用于汽车制造等领域。
本发明所述的 780MPa级冷轧双相带钢的制造方法， 在不增加任何工序 难度的情况下， 通过合理的成分设计和改良的制造歩骤， 就可以获得微观组 织均匀， 具备较好冷弯和扩孔性能， 力学性能各向异性小的高强度冷轧双相 带钢。 附图说明
图 1显示了实施例 3所涉及的 780MPa级冷轧双相带钢铸态的微观组织。 图 2显示了实施例 3所涉及的 780MPa级冷轧双相带钢的微观组织。 具体实施方式
根据具体实施例和说明书附图对本发明的技术方案作进一歩说明。 按照下述歩骤制造本发明所述的 780MPa级冷轧双相带钢：
1 ) 冶炼， 控制各化学元素的配比如表 1所示；
2) 铸造： 采用二冷水工艺， 喷水量不低于 0.7L水 /每公斤钢坯；
3 ) 热轧： 控制终轧温度为 820〜900°C， 轧后快速冷却；
4) 卷取： 控制卷取温度 450〜650°C ;
5 ) 冷轧， 冷轧压下率为 40〜60%；
6) 连续退火： 800〜860°C保温， 以不小于 5°C/s 的冷速冷却到 640〜 700°C之间， 再以 40〜100°C/s速度冷却到 220〜280°C之间， 在 220〜280°C 之间回火 100〜300s。
7) 平整， 平整率为 0.1〜0.4% (实施例 1没有进行该歩骤：)。 表 1
Figure imgf000008_0001
表 2显示了各实施例的具体工艺参数。其中实施例 2-1和实施例 2-2表 示均采用表 1所示的实施例 2的成分配比， 实施例 5-1和实施例 5-2表示均 采用表 1所示实施例 5的成分配比。
表 2
Figure imgf000008_0002
实施
0.85 850 500 800 10 700 280 80 270 150 0.2 例 2-1 实施
0.9 860 550 820 9 670 260 60 260 200 0.3 例 2-2 实施
0.95 890 600 840 6 680 240 50 240 100 0.4 例 3 实施
1 840 650 860 7 660 230 40 230 300 0.3 例 4 实施
0.82 880 610 850 5 640 220 45 220 250 0.2 例 5-1 实施
0.87 870 520 800 10 645 280 50 280 180 0.3 例 5-2 实施
0.93 900 570 835 8 650 270 70 240 120 0.1 例 6
表 3显示了本技术方案各实施例所涉及的冷轧双相钢的性能。
Figure imgf000009_0001
从表 3可以看出， 本发明所述的 780MPa级冷轧双相带钢： 具有较高的 强度， 良好的延伸率， 力学性能各向异性比较小， 能够取代 590MPa的冷轧 双相钢， 应用于汽车制造领域。
图 1显示了本案实施例 3的铸态微观组织， 图 2显示了本案实施例的微 观组织。 从图 1可以看出， 该冷轧双相钢的铸态组织为铁素体晶粒上弥散分 布的渗碳体。 从图 2可以看出， 该冷轧双相带钢的微观组织为细小的等轴状 铁素体基体以及在铁素体基体上均匀分布的马氏体岛， 带状组织轻微。 本技术领域中的普通技术人员应当认识到， 以上的实施例仅是用来说明 本发明， 而并非用作为对本发明的限定， 只要在本发明的实质精神范围内， 对以上所述实施例的变化、 变型都将落在本发明的权利要求书范围内。

Claims

权利要求书
1. 一种 780MPa级冷轧双相带钢， 其特征在于， 其微观组织为细小的等轴状 铁素体基体以及在铁素体基体上均匀分布的马氏体岛，且其化学元素质量 百分含量为：
C 0.06—0.1%；
Si ^0.28%；
Mn 1.8—2.3%；
Cr 0·卜 0.4%;
Mo Cr 0.3%时， 不添加； Cr<0.3%时， Mo=0.3-Cr; A1 0·015〜0·05%;
Nb、 Ti元素中的至少一种， 且 Nb+Ti在 0.02〜0.05%范围内； 余量为 Fe和其他不可避免的杂质。
2. 如权利要求 1 所述的 780MPa级冷轧双相带钢， 其特征在于， 其中： C 0·07〜0·09%; Mn 1.9—2.2%； A1 0·02〜0·04%。
3. 如权利要求 1或 2所述的 780MPa级冷轧双相带钢的制造方法，包括下列 歩骤：
1) 冶炼;
2) 铸造: 采用二冷水工艺， 喷水量不低于 0.7L水 /每公斤钢坯;
3) 热轧: 控制终轧温度为 820〜900°C， 轧后快速冷却；
4) 卷取: 控制卷取温度 450〜650°C；
5) 冷轧;
6) 连续 i
之间，再以 40〜100°C/s速度冷却到 220〜280°C之间，在 220〜280°C 之间回火 100〜300s。
4. 如权利要求 3所述的 780MPa级冷轧双相带钢的制造方法， 其特征在于， 还包括歩骤 7 ) 平整。
5. 如权利要求 4所述的 780MPa级冷轧双相带钢的制造方法， 其特征在于， 在所述歩骤 5 ) 中冷轧压下率为 40〜60%。
6. 如权利要求 4或 5所述的 780MPa级冷轧双相带钢的制造方法，其特征在 于， 所述歩骤 7) 中， 平整率为 0.1〜0.4%。
PCT/CN2013/076184 2013-01-22 2013-05-24 一种780MPa级冷轧双相带钢及其制造方法 Ceased WO2014114041A1 (zh)

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WO2016194272A1 (ja) * 2015-05-29 2016-12-08 Ｊｆｅスチール株式会社 高強度冷延鋼板、高強度めっき鋼板及びこれらの製造方法
US20180002771A1 (en) * 2014-12-19 2018-01-04 Posco High-strength cold rolled steel sheet with low material non-uniformity and excellent formability, hot dipped galvanized steel sheet, and manufacturing method therefor
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