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CN1215188C - Highly stable, steel and steel strips or steel sheets cold-formed, method for prodn. of steel strips and uses of said steel - Google Patents

Highly stable, steel and steel strips or steel sheets cold-formed, method for prodn. of steel strips and uses of said steel Download PDF

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CN1215188C
CN1215188C CNB028018923A CN02801892A CN1215188C CN 1215188 C CN1215188 C CN 1215188C CN B028018923 A CNB028018923 A CN B028018923A CN 02801892 A CN02801892 A CN 02801892A CN 1215188 C CN1215188 C CN 1215188C
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steel
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CN1463297A (en
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H·霍夫曼
B·恩格尔
M·曼恩
T·赫勒
W·齐默曼
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ThyssenKrupp Steel Europe AG
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ThyssenKrupp Stahl AG
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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
    • C22C38/06—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
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing 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
    • 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
    • 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
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • 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
    • 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
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0236—Cold 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
    • C21D8/0273—Final recrystallisation annealing

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

Abstract

介绍了一种具有良好冷成形性和高强度、由一种轻质钢构成的钢带或薄钢板，该轻质钢具有下述组成(以重量百分数计)：C：≤1.00%，Mn：7.00-30.00%，Al：1.00-10.00%，Si：＞2.50-8.00%，Al+Si：＞3.50-12.00%，B：＞0.00-＜0.01%，以及，任选地，Ni：＜8.00%，Cu：＜3.00%，N：＜0.60%，Nb：＜0.30%，Ti：＜0.30%，V：＜0.30%，P：＜0.01%，余者为Fe和不可避免的杂质。A steel strip or sheet with good cold formability and high strength, consisting of a lightweight steel having the following composition (in weight percent): C: ≤ 1.00%, Mn: 7.00-30.00%, Al: 1.00-10.00%, Si: >2.50-8.00%, Al+Si: >3.50-12.00%, B: >0.00-<0.01%, and, optionally, Ni: <8.00% , Cu: <3.00%, N: <0.60%, Nb: <0.30%, Ti: <0.30%, V: <0.30%, P: <0.01%, and the rest are Fe and unavoidable impurities.

Description

高强度、可冷成形的钢和钢带或薄钢板， 钢带的制备方法以及所述钢的用途High-strength, cold-formable steel and steel strip or sheet, process for producing steel strip and use of said steel

本发明涉及具有良好冷成形性能和高强度的Fe-Mn-Al-Si轻质钢材和钢带或薄钢板。此外，本发明还涉及由所述钢制备带材的方法以及该钢特别适合的用途。The invention relates to Fe-Mn-Al-Si light steel material and steel strip or thin steel plate with good cold forming performance and high strength. Furthermore, the invention relates to a method for producing strip from said steel and to the particularly suitable uses of this steel.

由德国专利197 27 759 C2已知一种用于制备车体部件和用于低温用途的轻质钢。该钢除Fe之外，还含有10-30％Mn，1-8％Al和1-6％Si，Al和Si含量之和不超过12％。在该已知钢中，碳含量，如果有，也只处于杂质范围。From German patent 197 27 759 C2 known a kind of light-weight steel that is used for producing car body parts and for cryogenic use. In addition to Fe, the steel also contains 10-30% Mn, 1-8% Al and 1-6% Si, and the sum of Al and Si content does not exceed 12%. In this known steel, the carbon content, if any, is only in the impurity range.

与之相反，在德国专利申请199 00 199 A1公布的轻质结构钢中，碳作为一种任选合金元素存在。该已知轻质钢含有大于7％但最多27％的Mn，大于1％但最多10％的Al，大于0.7％但最多4％的Si，＜0.5％C，＜10％Cr，＜10％Ni，以及＜0.3％Cu。另外，该钢可以含有N，V，Nb，Ti和P，这些元素之和不超过2％。In contrast, in the lightweight structural steels published in German Patent Application 199 00 199 A1, carbon is present as an optional alloying element. This known lightweight steel contains more than 7% but up to 27% Mn, more than 1% but up to 10% Al, more than 0.7% but up to 4% Si, < 0.5% C, < 10% Cr, < 10% Ni, and <0.3% Cu. In addition, the steel can contain N, V, Nb, Ti and P, and the sum of these elements does not exceed 2%.

欧洲专利申请1 067 203 A1公布的轻质钢也含有碳，其范围为0.001-1.6％。此外，除了铁，该钢还含有6-30％Mn，≤6％Al，≤2.5％Si，≤10％Cr，≤10％Ni和≤5％Cu。另外，该钢可以含有V，Ti，Nb，B，Zr和稀土元素，它们的含量之和不超过3％。该已知钢也可以含有P，Sn，Sb和As，这些元素的含量之和不高于0.2％。Lightweight steels published in European Patent Application 1 067 203 A1 also contain carbon in the range of 0.001-1.6%. In addition, in addition to iron, the steel also contains 6-30% Mn, ≤ 6% Al, ≤ 2.5% Si, ≤ 10% Cr, ≤ 10% Ni and ≤ 5% Cu. In addition, the steel can contain V, Ti, Nb, B, Zr and rare earth elements, and the sum of their contents does not exceed 3%. The known steel may also contain P, Sn, Sb and As, the sum of these elements not higher than 0.2%.

已表明：虽然存在碳，但具有这类组成的钢只能进行热轧而难于冷轧。因此，经常在带材棱边处看到不稳定相或裂纹，这使得实际上难于由这类钢大规模生产带材或薄板。而且，这类钢具有极强的各向同性变形特性，该特性用高的Эr值表示。由于成形性差，更难于对根据已知方法制备的薄钢板进一步加工。具有更高强度的可深度成形的钢对于制造带有齿或相当形状的组件的部件也是必须的。这些部件典型地是带有内齿或外齿的齿轮部件。通过流动成形可以低成本、高尺寸精度地制备所述部件。It has been shown that despite the presence of carbon, steels with such compositions can only be rolled hot and are difficult to cold roll. Consequently, unstable phases or cracks are often seen at the strip edges, which makes it practically difficult to mass-produce strips or sheets from such steels. Moreover, such steels have extremely strong isotropic deformation characteristics, which are indicated by high Эr values. Further processing of thin steel sheets produced according to known methods is more difficult due to poor formability. Deep formable steels with higher strength are also necessary for the manufacture of components with teeth or equivalently shaped components. These components are typically gear components with internal or external teeth. The parts can be produced cost-effectively with high dimensional accuracy by flow forming.

德国专利197 24 661 C2公开了一种通过流动成形制备齿轮部件的方法。根据该已知方法，由下屈服点至少500N/mm2的微合金化、高强度结构钢薄板制备出薄板坯。然后，通过流动成形将该板坯冷轧成齿轮。在形成齿的过程中，薄板材料重新变形最多至其成形能力的极限。随后，对带有齿的工件表面进行硬化，硬化时温度基本保持在不发生热变形的温度。German patent 197 24 661 C2 discloses a method for producing gear components by flow forming. According to this known method, a thin slab is produced from a microalloyed, high strength structural steel sheet having a lower yield point of at least 500 N/mm 2 . The slab is then cold rolled into gears by flow forming. During the formation of the teeth, the sheet material is re-deformed up to the limit of its formability. Subsequently, the surface of the workpiece with teeth is hardened, and the temperature during hardening is basically kept at a temperature where thermal deformation does not occur.

基于前述相关技术，本发明的目的是提供一种轻质钢和/或由其制备的具有良好成形性和良好强度、还容易工业规模生产的钢带或薄钢板。此外，还将涉及钢带或薄钢板的制备方法以及所述钢的优选用途。Based on the aforementioned related art, it is an object of the present invention to provide a lightweight steel and/or a steel strip or sheet produced therefrom having good formability and good strength, which is also easy to produce on an industrial scale. Furthermore, it will relate to the production method of the steel strip or sheet as well as the preferred use of said steel.

上述目的由一种轻质钢实现，该钢具有下述组成(以重量百分数计)：Above-mentioned purpose is realized by a kind of lightweight steel, and this steel has following composition (by weight percentage):

C：              ≤1.00％C: ≤1.00%

Mn：             7.00-30.00％Mn: 7.00-30.00%

Al：             1.00-10.00％Al: 1.00-10.00%

Si：             ＞2.50-8.00％Si: >2.50-8.00%

Al+Si：        ＞3.50-12.00％Al+Si: >3.50-12.00%

B：              ＞0.00-＜0.01％B: >0.00-<0.01%

以及，任选地and, optionally

Ni：             ＜8.00％Ni: ＜8.00%

Cu：             ＜3.00％Cu: ＜3.00%

N：              ＜0.60％N: <0.60%

Nb：             ＜0.30％Nb: <0.30%

Ti：             ＜0.30％Ti: <0.30%

V：              ＜0.30％V: <0.30%

P：              ＜0.01％P: <0.01%

余者为Fe和不可避免的杂质。这种情况下杂质包括硫和氧。The rest are Fe and unavoidable impurities. Impurities in this case include sulfur and oxygen.

令人惊奇地，已发现：有目的地添加硼会显著改善本发明钢的性能和可生产性。结果，根据本发明钢中存在的硼含量使屈服点降低，从而显著改善了成形性。如果根据本发明的钢中碳含量为0.10-1.00重量％，即：钢中可检测到的碳含量至少为0.10重量％，则上述元素对本发明钢的机械-技术性能的有利影响甚至可以进一步增强。Surprisingly, it has been found that the targeted addition of boron significantly improves the properties and producibility of the steel according to the invention. As a result, the boron content present in the steel according to the invention lowers the yield point and thus significantly improves the formability. The favorable influence of the aforementioned elements on the mechanical-technical properties of the steel according to the invention can be even further enhanced if the carbon content in the steel according to the invention is 0.10-1.00% by weight, i.e. the detectable carbon content in the steel is at least 0.10% by weight .

在这种情况下，这些元素的存在可以获得特别良好的机械性能与技术性能的组合。因此，与由此处述及的相关技术了解的薄钢板相比，根据本发明的钢和/或由其制备的钢带或薄钢板具有显著降低的Эr值。In this case, the presence of these elements makes it possible to obtain a particularly good combination of mechanical and technical properties. Accordingly, the steel according to the invention and/or the steel strip or sheet produced therefrom has a significantly lower Эr value than the steel sheet known from the related art mentioned here.

此外，具有根据本发明的组成的冷轧钢带和薄钢板的特征包括：较低的屈服点、高硬化指数(n值)下改善的拉伸成形性、较高的深拉拔质量(r值)和较低的平面各向异性(Эr值)以及较高的屈服点与延伸率之积。结果，根据本发明的钢带和薄钢板的抗拉强度至少680MPa，屈服点与延伸率之积至少41000MPa。根据本发明的薄钢板和钢带的屈服点不超过520MPa。同时，根据本发明的钢和/或由其制备的薄板和带材具有20％，最高超过45％的格外高的均匀延伸率。n值最高可达0.7。Furthermore, cold-rolled steel strips and sheets with compositions according to the invention are characterized by lower yield points, improved stretch formability at high hardening exponents (n-values), higher deep-drawing qualities (r value) and lower plane anisotropy (Эr value) and higher product of yield point and elongation. As a result, the steel strip and sheet according to the invention have a tensile strength of at least 680 MPa and a product of yield point and elongation of at least 41000 MPa. The yield point of the steel sheets and strips according to the invention does not exceed 520 MPa. At the same time, the steel according to the invention and/or the sheets and strips produced therefrom have an exceptionally high uniform elongation of 20%, up to more than 45%. The value of n can be up to 0.7.

结果，这样就获得了冷成形性特别良好的轻质钢带或薄钢板，由于其具有较高的强度和较低的密度，因此特别适于制备汽车车身部件。突出的强度与重量比也使得根据本发明制备的薄钢板适于制备车辆，尤其是汽车车辆的车轮，适于制备内部或外部液压成形的部件，适于制备高强度发动机部件如凸轮轴或活塞连杆，适于制备用来阻挡脉冲应力如爆炸的部件，例如装甲板，以及适于制备专门用于保护人类不受爆炸伤害的保护性部件。特别是在所述后面的应用中，根据本发明的薄钢板的较低重量和同时具有的较高强度效果很好。As a result, lightweight steel strips or sheets with particularly good cold formability are obtained which are particularly suitable for the production of automotive body parts due to their high strength and low density. The outstanding strength-to-weight ratio also makes the thin steel sheets produced according to the invention suitable for the production of wheels for vehicles, especially automotive vehicles, for the production of internal or external hydroformed components, for the production of high-strength engine components such as camshafts or pistons Connecting rods, suitable for the preparation of parts for resisting impulse stresses such as explosions, such as armor plates, and for the preparation of protective parts specially designed to protect humans from blasts. Especially in said latter applications, the lower weight and simultaneously higher strength of the steel sheets according to the invention work well.

根据本发明的薄钢板如果具有纯奥氏体组织结构，还尤其适于制备非磁性部件。The thin steel sheets according to the invention are also particularly suitable for the production of non-magnetic components if they have a purely austenitic structure.

另外，已发现：根据本发明的钢甚至在极低温度下也能保持其强度。因此，它们特别适于制备用于低温工程的部件，例如用于低温工程的容器或管道。Furthermore, it has been found that the steel according to the invention retains its strength even at very low temperatures. They are therefore particularly suitable for the production of components for cryogenic engineering, for example vessels or pipes for cryogenic engineering.

如果硼含量为0.002-0.01重量％，尤其是0.003-0.008重量％，则能够特别可靠地获得硼在根据本发明的钢中的有利作用。The beneficial effect of boron in the steel according to the invention can be achieved particularly reliably if the boron content is 0.002-0.01% by weight, in particular 0.003-0.008% by weight.

碳含量为0.1-1.0％，也能确保提高根据本发明的薄钢板和钢带的可生产性。在根据本发明的钢中，由于存在碳，金属间化合物的形成受到抑制。因此使在由已知钢制备的钢带中存在的带棱边区开裂和不稳定相显著减少，尤其是随着C含量的增加，所述不稳定相减少。添加硼可进一步改善带材棱边质量。结果，由于C和B的共同添加，带材棱边的不稳定相几乎可完全避免。A carbon content of 0.1-1.0% also ensures increased producibility of the steel sheets and strips according to the invention. In the steel according to the invention, the formation of intermetallic compounds is suppressed due to the presence of carbon. As a result, the occurrence of edge zone cracking and unstable phases in steel strips produced from known steels is considerably reduced, especially with increasing C content. Addition of boron can further improve strip edge quality. As a result, the unstable phase at the edge of the strip is almost completely avoided due to the co-addition of C and B.

在对机械-技术性能的影响上硼可作为合金元素Mn的替代元素。结果，已证实：含有20％Mn和0.003％B的钢的性能分布与含25％Mn但不含B的钢相似。因此，根据本发明的轻质结构钢可以具有较低的Mn含量，但仍具有较高的强度。这会导致合金元素成本降低，而且，还能够使本发明使用的轻质钢的熔炼冶金制备更为容易。Boron can be used as a substitute element for the alloying element Mn in terms of its influence on the mechanical-technical properties. As a result, it was confirmed that the property distribution of the steel containing 20% Mn and 0.003% B was similar to that of the steel containing 25% Mn but no B. Therefore, the lightweight structural steel according to the present invention can have a lower Mn content, but still have a higher strength. This results in a lower cost of the alloying elements and also enables easier smelt-metallurgical preparation of the lightweight steel used in the present invention.

此外，本发明提供的C和B的含量容许采用宽范围的热轧参量。结果，已表明：当所选择的热轧终了温度和卷取温度较高时获得的根据本发明的钢的特性与在热轧终了温度和卷取温度较较低时获得的特性基本一致。这种热轧带材期间的不敏感性也有利于容易制备根据本发明的薄钢板。Furthermore, the C and B levels provided by the present invention allow the use of a wide range of hot rolling parameters. As a result, it has been shown that the properties of the steel according to the invention obtained when the selected hot-rolling end temperature and coiling temperature are higher are substantially identical to those obtained when the hot-rolling end temperature and coiling temperature are lower. This insensitivity during hot rolling of the strip also contributes to the easy production of the thin steel sheets according to the invention.

由于将Si含量限制在2.50重量％以上，优选在2.70重量％以上，因此，与Si含量较低的轻质钢带或薄板相比，根据本发明的钢带和薄钢板具有改善的冷成形性。较高的Si含量意味着更均匀的屈服点和抗拉强度值，还意味着更高的断裂时的延伸率和均匀延伸率。此外，根据本发明的钢中的Si导致更高的r和n值，还能够获得各向均匀的机械性能。Al与Si含量之和的上限为12％，原因是Al与Si含量之和超过此极限会产生脆化的危险。Due to the limitation of the Si content above 2.50% by weight, preferably above 2.70% by weight, the steel strip and sheet according to the invention have improved cold formability compared to lightweight steel strip or sheet with a lower Si content . Higher Si content means more uniform yield point and tensile strength values and also higher elongation at break and uniform elongation. Furthermore, Si in the steel according to the invention leads to higher r and n values, also enabling isotropically homogeneous mechanical properties. The upper limit of the sum of Al and Si content is 12%, because the sum of Al and Si content exceeding this limit creates the risk of embrittlement.

根据本发明的钢带和薄板优选采用下述方法制备，该方法中：浇注出由具有上述组成的本发明的钢制备的进料毛坯，例如板坯、薄板坯或带材，将浇注的进料毛坯加热到1100℃或者在该温度下直接使用，将预热的进料毛坯热轧成热轧带材，其中热轧终了温度至少800℃，以及，在450-700℃的卷取温度下对所述终轧的热轧带材进行卷取。The steel strip and sheet according to the invention are preferably produced by a method in which a feed blank, such as a slab, thin slab or strip, prepared from the steel according to the invention having the composition described above is cast, the cast feed The raw material blank is heated to 1100°C or used directly at this temperature, and the preheated feed blank is hot-rolled into a hot-rolled strip, wherein the hot-rolling end temperature is at least 800°C, and, at a coiling temperature of 450-700°C The finished hot-rolled strip is coiled.

由于所述热轧带材在至少800℃的热轧终了温度下热轧和在根据本发明的较低温度下进行卷取，因此，碳和，尤其是前述硼的有利作用得以充分发挥。结果，硼和碳使在该范围热轧的带材具有较高的抗拉强度和屈服点，而其断裂时的延伸率仍然可以接受。随着热轧终了温度的提高，抗拉强度和屈服点均下降，而延伸率增大。通过在本发明给定的范围内改变热轧终了温度，可以容易且有目的地影响所要求的钢带性能。Due to the fact that the hot-rolled strip is hot-rolled at a hot-rolling finish temperature of at least 800° C. and coiled at a lower temperature according to the invention, the beneficial effects of carbon and, in particular, the aforementioned boron are fully exploited. As a result, boron and carbon give strip hot-rolled in this range high tensile strength and yield point while still having acceptable elongation at break. With the increase of hot rolling end temperature, the tensile strength and yield point both decreased, while the elongation increased. By varying the hot rolling finish temperature within the range given by the invention, the desired properties of the strip can be easily and purposefully influenced.

通过限制卷取温度至多700℃能够可靠地避免材料发生脆化。已表明：当卷取温度较高时形成脆性相，这例如可能使材料发生剥落，并且因此使进一步的加工变得更为困难或者甚至不可能。Embrittlement of the material can be reliably avoided by limiting the coiling temperature to at most 700°C. It has been shown that at higher coiling temperatures brittle phases form, which can, for example, cause the material to flake off and thus make further processing more difficult or even impossible.

根据本发明的热轧带材的特征甚至在于其良好的使用性能。如果制备较薄的薄板或带材，则可以在卷取之后将热轧带材冷轧成冷轧带材，冷轧优选以30-75％的压下量进行。随后优选对所获得的冷轧带材进行退火，退火温度为600-1100℃。这时退火可以在炉罩内，600-750℃下进行，或者在退火炉内，750-1100℃下连续进行。最后，在最后步骤对冷轧带材进行矫正(dressing)，这有利于冷成形性和表面结构的获得。The hot-rolled strip according to the invention is even characterized by its good service properties. If thinner sheets or strips are produced, the hot-rolled strip can be cold-rolled to cold-rolled strip after coiling, preferably at a reduction of 30-75%. The obtained cold-rolled strip is then preferably annealed at a temperature of 600-1100°C. At this time, the annealing can be carried out in the furnace cover at 600-750°C, or continuously in the annealing furnace at 750-1100°C. Finally, the cold-rolled strip is dressed in the final step, which facilitates the cold formability and the acquisition of the surface structure.

根据本发明的钢和/或由其制备的钢带和薄板的另一种特别有利的用途是通过流动成形制备冷成形部件。为此，由所述钢制备出板坯，然后，通过流动成形(flow forming)完成终加工。由于其特殊的性能分布，根据本发明的钢和/或由其制备的薄板坯特别适于此目的。Another particularly advantageous use of the steel according to the invention and/or the steel strips and sheets produced therefrom is the production of cold-formed parts by flow forming. To this end, slabs are produced from the steel and then finished by flow forming. Due to its special property profile, the steel according to the invention and/or the thin slabs produced therefrom are particularly suitable for this purpose.

依据组成不同，根据本发明的钢的显微组织或者是纯奥氏体，或者是包含马氏体组元的铁素体与奥氏体的混合物。因此，根据本发明的钢的成形性能显著提高。与已知用于通过流动成形制备的高强度微合金化或多相钢相比，其可以在冷成形过程中进行更为强烈的压制。结果，依据冷成形条件，部件强度可以达1400-2200N/mm2。因此，可以省去对冷成形后获得的部件进行附加的硬化处理。如果轻元素如Si和Al含量较高，故根据本发明使用的钢密度较低，结果该钢对于特定目的，尤其是齿形齿轮部件的制备也很有利。Depending on the composition, the microstructure of the steel according to the invention is either pure austenite or a mixture of ferrite and austenite containing martensitic components. Consequently, the formability of the steel according to the invention is significantly improved. It can be pressed more intensely during cold forming than is known for high strength microalloyed or multiphase steels produced by flow forming. As a result, part strengths of 1400-2200 N/mm 2 can be achieved depending on cold forming conditions. Additional hardening of the components obtained after cold forming can thus be dispensed with. The steel used according to the invention has a lower density if the content of light elements such as Si and Al is higher, with the result that the steel is also advantageous for special purposes, especially the production of toothed gear components.

如果使用具有根据本发明组成并且根据本发明制备的钢，则可以免于对流动成形的部件进行热处理或表面硬化处理。如果根据本发明的钢用于制备使用期间受到强烈局部应力作用的齿形部件，那么，将不再存在现有技术中由上述附加处理步骤引起的变形和起鳞的危险。结果，根据本发明的钢能够通过冷成形，特别是流动成形低成本地制备轻质、重载且尺寸稳定的部件。If a steel with a composition according to the invention and produced according to the invention is used, heat treatment or surface hardening of the flow-formed component can be dispensed with. If the steel according to the invention is used for the production of toothed parts which are subjected to strong local stresses during use, there is no longer the risk of deformation and scaling as in the prior art caused by the above-mentioned additional processing steps. As a result, the steel according to the invention enables the inexpensive production of lightweight, heavy-duty and dimensionally stable components by cold forming, in particular flow forming.

下面，参照示例性实施方案和对比实例对本发明进行更详细介绍。Hereinafter, the present invention will be described in more detail with reference to exemplary embodiments and comparative examples.

表1中示出了四种钢A，B，C，D和E的组成，钢A，B和C对应的是根据本发明提供的合金，而钢D和E则是对比实例。Table 1 shows the composition of four steels A, B, C, D and E, steels A, B and C correspond to alloys provided according to the present invention, while steels D and E are comparative examples.

表1   钢     C    Mn    Al    Si        B  Fe，杂质   A     0.5    15     3     3      0.003    余量   B     0.5    20     3     3      0.003    余量   C     -    20     3     3      0.003    余量   D     -    14     3     3       -    余量   E     -    19     3     3       -    余量 Table 1 steel C mn Al Si B Fe, impurity A 0.5 15 3 3 0.003 margin B 0.5 20 3 3 0.003 margin C - 20 3 3 0.003 margin D. - 14 3 3 - margin E. - 19 3 3 - margin

将具有所述组成的钢A-E熔化并浇注成板坯。随后，将该板坯预热至1150℃。然后，对所述预热的板坯热轧并随后进行卷取。Steels A-E having the stated compositions were melted and cast into slabs. Subsequently, the slab was preheated to 1150°C. The preheated slab is then hot rolled and subsequently coiled.

表2中列出了各个热轧终了温度ET，卷取温度HT，以及获得的热轧带材的抗拉强度Rm、屈服点Re、A50延伸率、均匀延伸率Ag1和n值等各种性能。Table 2 lists the hot rolling end temperature ET, the coiling temperature HT, and the obtained hot-rolled strip tensile strength Rm, yield point Re, A 50 elongation, uniform elongation A g1 and n value, etc. performance.

表2   钢  ET[℃]   HT[℃]     Re[N/mm2]     Rm[N/mm2]   A50[％]     Ag1[％]      n   A    960    500     486     792    42     38     0.31   B    930    500     509     825    46     42     0.32   C    920    500     496     818    31     27     -   D    820    500     610     920    26     -     -   E    840    500     430     700    30     -     - Table 2 steel ET[°C] HT[°C] Re[N/mm 2 ] Rm[N/mm 2 ] A 50 [%] A g1 [%] no A 960 500 486 792 42 38 0.31 B 930 500 509 825 46 42 0.32 C 920 500 496 818 31 27 - D. 820 500 610 920 26 - - E. 840 500 430 700 30 - -

由不是根据本发明的钢D制备的带材不能进行冷轧，除此之外，对所获得的其他热轧带材随后在约65％的变形度下进行冷轧，并且在950℃下进行连续退火。表3中列出了以这种方式获得的冷轧薄钢板的机械性能。Strips produced from steel D not according to the invention cannot be cold-rolled, other hot-rolled strips obtained are subsequently cold-rolled at a degree of deformation of about 65% and at 950°C continuous annealing. Table 3 lists the mechanical properties of the cold-rolled steel sheets obtained in this way.

表3  钢      Re[N/mm2]      Rm[N/mm2]     A50[％]     Ag1[％]     n     r     Эr   A     408      775     64      64    0.33    1.02     -0.1   B     411      785    61.1     61.1    0.33    1.0     -0.06   C     284      714     58     56.8    0.39    1.05     -0.17   D                                     不能冷轧   E     382      744    52.5     50.3    0.32    0.82     -0.25 table 3 steel Re[N/mm 2 ] Rm[N/mm 2 ] A 50 [%] A g1 [%] no r Эr A 408 775 64 64 0.33 1.02 -0.1 B 411 785 61.1 61.1 0.33 1.0 -0.06 C 284 714 58 56.8 0.39 1.05 -0.17 D. Can not be cold rolled E. 382 744 52.5 50.3 0.32 0.82 -0.25

结果表明：根据本发明由钢A-C制备的钢带具有突出的冷成形性能。在这种情形下，在具有高的强度和高的断裂延伸率的同时，各钢带均具有显著的各向同性变形特性(r～1，Эr～0)。即使由根据本发明的钢C制备的带材中不含碳但含有硼，其仍然具有较低的屈服点、较高的断裂和均匀延伸率以及各向同性成形性能。The results show that the steel strips produced according to the invention from steels A-C have outstanding cold forming properties. In this case, while having high strength and high elongation at break, each steel strip has remarkable isotropic deformation characteristics (r~1, Эr~0). Even if the strip produced from steel C according to the invention contains no carbon but contains boron, it still has a lower yield point, higher fracture and uniform elongation and isotropic formability.

因此，根据本发明的薄钢板的所有变化均特别适于制备车身部件，尤其是车身的外面板，适于制备车辆，尤其是汽车车辆的车轮，适于制备非磁性部件，适于制备用于低温工程的容器，适于制备内部或外部液压成形的部件，适于制备专门用于制造高强度发动机部件如凸轮轴或活塞连杆的管件，适于制备用来阻挡脉冲应力如爆炸的部件、或保护性部件如装甲板，或者用于人或动物身体的身体用盔甲。也可以由根据本发明的薄钢板制备特征为重量轻且使用性能良好的重载齿轮部件，而不需要进行附加的热处理。All variants of the thin steel sheet according to the invention are therefore particularly suitable for the production of body parts, in particular outer panels of vehicle bodies, for the production of vehicles, especially wheels for motor vehicles, for the production of non-magnetic parts, for the production of Vessels for cryogenic engineering, suitable for the preparation of internal or external hydroformed parts, suitable for the preparation of pipes specially used for the manufacture of high-strength engine parts such as camshafts or piston connecting rods, suitable for the preparation of parts used to resist impulse stresses such as explosions, Or protective parts such as armor plates, or body armor for the human or animal body. Heavy-duty gear components characterized by low weight and good serviceability can also be produced from the thin steel sheet according to the invention without additional heat treatment.

Claims (39)

1. one kind has good cold formability and high-intensity lightweight steel, and it has following composition (by weight percentage):
C： ≤1.00％
Mn： 7.00-30.00％
Al： 1.00-10.00％
Si： ＞2.50-8.00％
Al+Si： ＞3.50-12.00％
B： ＞0.00-＜0.01％
And, perhaps
Ni： ＜8.00％
Cu： ＜3.00％
N： ＜0.60％
Nb： ＜0.30％
Ti： ＜0.30％
V： ＜0.30％
P： ＜0.01％
The rest is Fe and unavoidable impurities.
2. according to the lightweight steel of claim 1, it is characterized in that: carbon content is 0.10-1.00 weight %.
3. according to the lightweight steel of claim 1, it is characterized in that: Si content is greater than 2.70 weight %.
4. according to the lightweight steel of claim 1, it is characterized in that: boron content is 0.002-0.01 weight %.
5. according to the lightweight steel of claim 4, it is characterized in that: boron content is 0.003-0.008 weight %.
6. by having steel band or the steel sheet that is equipped with according to one of among the claim 1-5 the steel of forming.
7. according to the steel band or the steel sheet of claim 6, it is characterized in that: its tensile strength is 680MPa at least.
8. according to the steel band or the steel sheet of claim 6, it is characterized in that: the long-pending 41000MPa at least of its tensile strength and unit elongation.
9. according to the steel band or the steel sheet of claim 6, it is characterized in that: the maximum 520MPa of its yield-point.
10. capable of cold forming, high-strength steel strip or steel-sheet preparation method, wherein:
-outpour the charging blank by having to water according to one of among the claim 1-5 the steel of forming,
-the charging blank of cast is heated to more than or equal to 1100 ℃ or directly use under this temperature,
-the charging blank of preheating is rolled into hot rolled band, wherein temperature of hot-rolled end is at least 800 ℃, and,
-hot rolled band to described finish to gauge under 450-700 ℃ coiling temperature batches.
11. the method according to claim 10 is characterized in that: described charging blank is slab, thin slab or band.
12. the method according to claim 10 is characterized in that: after batching with the cold rolling one-tenth cold-strip of hot rolled band.
13. the method according to claim 12 is characterized in that: under 600-1100 ℃ annealing temperature, cold-strip is annealed.
14. the method according to claim 13 is characterized in that: with the bonnet annealing way, described annealing is carried out under 600-750 ℃ annealing temperature.
15. the method according to claim 13 is characterized in that: with continuous annealing mode, described annealing is carried out under 750-1100 ℃ annealing temperature.
16. the method according to claim 11 is characterized in that: described cold-strip is flattened.
17. the method according to claim 11 is characterized in that: cold rolling cold roling reduction with 30-75% carries out.
18. according to one of among the claim 10-17 method, it is characterized in that: the slab with cold rolling one-tenth component end item is prepared from by the corresponding hot rolling band or the cold rolling strap that are obtained subsequently.
19. the method according to claim 18 is characterized in that: the cold shaping of being implemented is a flow forming.
20. by steel or steel band or the purposes of steel sheet in preparation supported cart body component according to one of among the claim 1-9.
21. by steel or steel band or the purposes of steel sheet in the external visual part of preparation car body according to one of among the claim 1-9.
22. by steel or steel band or the purposes of steel sheet in the wheel of preparation vehicle according to one of among the claim 1-9.
23. the purposes according to claim 21 is characterized in that: described vehicle is an automobile.
24. by steel or steel band or the purposes of steel sheet in the preparation non-magnetic part according to one of among the claim 1-9.
25. by the purposes that is used for the parts of cryogenic engineering according to one of among the claim 1-9 steel or steel band or steel sheet in preparation.
26. by according to one of among the claim 1-9 steel or steel band or the steel sheet purposes in the parts that preparation inside or external hydraulic are shaped.
27. by steel or steel band or the purposes of steel sheet in the preparation pipe fitting according to one of among the claim 1-9.
28. the purposes according to claim 27 is characterized in that: described pipe fitting is used to make the high strength engine parts.
29. the purposes according to claim 27 is characterized in that: described engine parts are camshaft or piston rod.
30. by the purposes that is used for stopping the parts of pulse stress according to one of among the claim 1-9 steel or steel band or steel sheet in preparation.
31. the purposes according to claim 30 is characterized in that: described parts are armor plates.
32. the purposes according to claim 30 or 31 is characterized in that: described pulse stress is blast.
33. by being used for protecting the person not to be subjected to the purposes of the protectiveness parts of pulse stress in preparation according to one of among the claim 1-9 steel or steel band or steel sheet.
34. the purposes according to claim 33 is characterized in that: described protectiveness parts are the helmet or body armor.
35. the purposes according to claim 33 or 34 is characterized in that: described pulse stress is blast.
36. by according to one of among the claim 1-9 steel or steel band or steel sheet in the purposes for preparing by flow forming in the parts.
37. by steel or steel band or the purposes of steel sheet in the preparation geared parts according to one of among the claim 1-9.
38. the purposes according to claim 37 is characterized in that: described geared parts has tooth.
39. the purposes according to claim 37 or 38 is characterized in that: described geared parts is prepared from by flow forming.
CNB028018923A 2001-06-13 2002-06-13 Highly stable, steel and steel strips or steel sheets cold-formed, method for prodn. of steel strips and uses of said steel Expired - Fee Related CN1215188C (en)

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