JP5232793B2 - Method for producing a flat steel product from steel forming a composite phase microstructure - Google Patents
Method for producing a flat steel product from steel forming a composite phase microstructure Download PDFInfo
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- JP5232793B2 JP5232793B2 JP2009533820A JP2009533820A JP5232793B2 JP 5232793 B2 JP5232793 B2 JP 5232793B2 JP 2009533820 A JP2009533820 A JP 2009533820A JP 2009533820 A JP2009533820 A JP 2009533820A JP 5232793 B2 JP5232793 B2 JP 5232793B2
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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
- 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
- C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
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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
- 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
- C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
- C21D8/041—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing involving a particular fabrication or treatment of ingot or slab
- C21D8/0415—Rapid solidification; Thin strip casting
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- 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
- B22D11/001—Continuous casting of metals, i.e. casting in indefinite lengths of specific alloys
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- 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
- B22D11/06—Continuous casting of metals, i.e. casting in indefinite lengths into moulds with travelling walls, e.g. with rolls, plates, belts, caterpillars
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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
- 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
- C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
- C21D8/0421—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the working steps
- C21D8/0426—Hot rolling
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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
- 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
- C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
- C21D8/0447—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment
- C21D8/0473—Final recrystallisation annealing
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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
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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
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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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
- C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
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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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
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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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/001—Austenite
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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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/002—Bainite
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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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/008—Martensite
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- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Heat Treatment Of Sheet Steel (AREA)
- Metal Rolling (AREA)
- Heat Treatment Of Steel (AREA)
- Treatment Of Steel In Its Molten State (AREA)
Abstract
Description
本発明は、高張力複合相鋼(hochfeste Komplexphasenstaehlen)から、フラット鋼生成物(Stahl-Flachprodukte;例えば、ストリップ又はシートメタルブランク)を製造する方法に関する。前記CP鋼は、多相鋼の群に属する。これらは、通常、ミクロ組織の相のタイプ、量、及び配置(Anordnung)によりその特性が決定される鋼に関する。従って、ミクロ組織中には、少なくとも2つの相(例えば、フェライト、マルテンサイト、ベイナイト)が存在する。その結果、これらは、通常の鋼と比較すると、優れた強度/成形性の組合せを有する。 The present invention relates to a method for producing a flat steel product (Stahl-Flachprodukte; for example, a strip or sheet metal blank) from a high tensile composite phase steel (hochfeste Komplexphasenstaehlen). The CP steel belongs to the group of multiphase steels. These usually relate to steels whose properties are determined by the type, amount, and arrangement of microstructure phases. Therefore, there are at least two phases (eg, ferrite, martensite, bainite) in the microstructure. As a result, they have an excellent strength / formability combination when compared to ordinary steel.
多相鋼は、これらの特殊な特徴のために、特に自動車製造にとって極めて興味深い。なぜなら、それらの強度が高いために、一方で、より小さい材料厚の使用が可能になると同時に、車両重量の削減を可能にし、そして、他方で、衝突の際の車体の安全性(衝突態様)を改良するからである。従って、ボディ全体の少なくとも均等な強度を有する多相鋼によって、前記多相鋼製の部品のシートメタル厚を、従来の鋼製のボディよりも減少させることができる。 Multiphase steels are particularly interesting for automobile manufacturing because of these special features. Because of their high strength, on the one hand, it is possible to use a smaller material thickness, while at the same time enabling a reduction in vehicle weight, and on the other hand, the safety of the vehicle body in the event of a collision (collision mode) It is because it improves. Accordingly, the sheet metal thickness of the multi-phase steel part can be reduced as compared with the conventional steel body by the multi-phase steel having at least equal strength of the entire body.
通常、多相鋼は、コンバータースチールミル(Konverterstahlwerk)中で溶融され、そして、連続鋳造機でスラブ又は薄スラブへ鋳造され、次に、熱間圧延ストリップへ熱間圧延されて、巻き取られる。この場合には、特定のミクロ組織フラクションを調節する目的で、熱間圧延後での熱間圧延ストリップの選択的に制御された冷却によって、熱間圧延ストリップの機械的特性を変化させることができる。熱間圧延ストリップを冷間圧延ストリップへ冷間圧延して、より薄いシートメタル厚を得ることもできる(EP0910675B1、EP0966547B1、EP1169486B1、EP1319725B1、EP1398390A1)。 Usually, the multiphase steel is melted in a converter steel mill (Konverterstahlwerk) and cast into a slab or thin slab in a continuous caster and then hot rolled into a hot rolled strip and wound up. In this case, the mechanical properties of the hot-rolled strip can be changed by selectively controlled cooling of the hot-rolled strip after hot rolling in order to adjust the specific microstructure fraction. . It is also possible to cold roll a hot rolled strip into a cold rolled strip to obtain a thinner sheet metal thickness (EP0910675B1, EP0966547B1, EP1169486B1, EP13197725B1, EP1398390A1).
前記製造手段では、特に、包晶凝固する組成の鋳造で問題が生じる。これらの鋼の品質(Stahlguete)の場合には、連続鋳造間で縦方向の亀裂が生じるリスクがある。前記縦方向の亀裂の出現は、鋳造されたスラブ又は薄スラブから製造される熱間圧延ストリップの品質を低下させ、使用不可能にすることができる。このリスクを防止するために、大規模な対策(例えば、増加した火炎処理)が必要であり、それによって、前記鋼品質を不経済的なものへ転換させてしまう。高いAl含有量を有する鋳造鋼の場合には、粉末化フラックス(Giesspulver)での相互作用によって望ましくない効果も生じ、その結果、前記鋼製のフラット生成物の品質もネガティブな影響を受ける。 In the manufacturing means, there is a problem particularly in casting with a composition that peritectic solidifies. In the case of the quality of these steels (Stahlguete) there is a risk of longitudinal cracks occurring between continuous castings. The appearance of the longitudinal cracks can degrade the quality of hot rolled strips made from cast or thin slabs and render them unusable. In order to prevent this risk, large-scale measures (for example, increased flame treatment) are required, thereby converting the steel quality to uneconomical. In the case of cast steel with a high Al content, undesirable effects are also produced by the interaction with the powdered flux (Giesspulver), with the result that the quality of the flat product made of steel is also negatively affected.
高張力多相鋼からフラット生成物を製造することについての更なる問題は、前記鋼を圧延する際に、高い圧延力を付与する必要があることである。前記要件のために、通常、一般に入手可能な現在の製造機では、前記タイプの鋼から製造される高張力熱間圧延ストリップが、自動車産業により現在要求される要件を十分に満たさない幅及び厚さでしか、製造できないということが結果として生じる。十分な幅で厚さの小さいストリップについての追加的な需要がある。更に、従来の方法によって、800MPaを超える強度を有する冷間圧延ストリップを多相鋼から製造することが実際に困難であることが分かっている。 A further problem with producing flat products from high-strength multiphase steels is that when rolling the steel, it is necessary to apply a high rolling force. Because of the above requirements, current production machines that are generally available generally have a width and thickness that does not sufficiently meet the requirements currently required by the automotive industry for high-tensile hot-rolled strips made from said type of steel. Only then can it be produced. There is an additional demand for strips of sufficient width and thickness. Furthermore, it has proved practically difficult to produce cold-rolled strips with a strength exceeding 800 MPa from multiphase steel by conventional methods.
多相鋼から鋼ストリップを製造するための代替的な方法が、欧州特許EP1072689B1(DE60009611T2)中に提案されている。薄い鋼ストリップを製造するこの公知方法によると、最初に、(以下、重量%で表示)C:0.05及び0.25%;Mn、Cu及びNi:合計で0.5〜3%;Si及びAl:合計で0.1〜4%;P、Sn、As及びSb:合計で0.1%まで;Ti、Nb、V、Zr及び希土類金属元素(REM):合計で0.3%未満;並びに、Cr、Mo及びV:それぞれ1%未満;残余鉄及び不可避の不純物を含む鋼メルトを、厚さ0.5〜10mm(特に、1〜5mm)を有する鋳造ストリップへ鋳造する。続いて、25%〜70%の間の範囲にある変形度(Umformgrad)で、鋳造ストリップを熱間圧延ストリップへ1回又は複数回のパスでインラインに熱間圧延する。この場合、最終熱間圧延温度は、Ar3温度を超える。熱間圧延の終了時点で、得られる熱間圧延ストリップは、次に、2つの工程で冷却される。前記冷却の最初の工程では、温度が400〜550℃の間の範囲に達するまで、冷却速度5〜100℃/秒が維持される。次に、前記温度で、熱間圧延ストリップを滞留時間保持する。前記滞留時間は、5%を超える残余オーステナイト含有量を有する鋼がベイナイト変態するために必要とされる時間である。この場合、パーライトの形成も避けられるべきである。所望のミクロ組織を得るのに十分な滞留時間後で、変態プロセスが第2冷却工程の始まりによって中断される。前記第2冷却工程では、熱間圧延ストリップを400℃未満の温度にして、350℃未満の巻き取り温度でコイルに巻き取る。 An alternative method for producing steel strips from multiphase steel has been proposed in European patent EP 1072689B1 (DE 60009611T2). According to this known method of producing a thin steel strip, first (hereinafter expressed in weight percent) C: 0.05 and 0.25%; Mn, Cu and Ni: 0.5-3% in total; Si And Al: 0.1 to 4% in total; P, Sn, As and Sb: up to 0.1% in total; Ti, Nb, V, Zr and rare earth metal elements (REM): less than 0.3% in total And Cr, Mo and V: each less than 1%; a steel melt containing residual iron and inevitable impurities is cast into cast strips having a thickness of 0.5 to 10 mm (especially 1 to 5 mm). Subsequently, the cast strip is hot rolled inline in one or more passes to the hot rolled strip with a degree of deformation (Umformgrad) in the range between 25% and 70%. In this case, the final hot rolling temperature exceeds the Ar 3 temperature. At the end of hot rolling, the resulting hot rolled strip is then cooled in two steps. In the first step of cooling, a cooling rate of 5-100 ° C./sec is maintained until the temperature reaches a range between 400-550 ° C. The hot rolled strip is then held at that temperature. The residence time is the time required for a steel having a residual austenite content of more than 5% to undergo bainite transformation. In this case, the formation of pearlite should also be avoided. After a residence time sufficient to obtain the desired microstructure, the transformation process is interrupted by the beginning of the second cooling step. In the second cooling step, the hot-rolled strip is brought to a temperature of less than 400 ° C. and wound around the coil at a winding temperature of less than 350 ° C.
EP1072689B1に記載される方法では、TRIP特性(TRIP=変態誘起塑性)を有し、そして、ベイナイトミクロ組織フラクションを有する熱間圧延ストリップを、多相鋼から単純な方法で製造することができる。前記鋼は、良好な成形性を有する比較的高い強度を有する。しかしながら、多くの用途(特に、自動車製造分野における)にとって、強度が不十分である。 In the method described in EP 1072689 B1, hot-rolled strips having TRIP properties (TRIP = transformation induced plasticity) and having a bainite microstructure fraction can be produced in a simple manner from multiphase steel. The steel has a relatively high strength with good formability. However, for many applications (especially in the field of automobile production) the strength is insufficient.
従って、本発明の目的は、高張力フラット鋼生成物を、少ない労力で、幾何学的寸法の広い範囲で、製造することを可能にする方法を提供することからなる。 The object of the invention therefore consists in providing a method which makes it possible to produce high-tensile flat steel products with a small amount of effort and in a wide range of geometric dimensions.
前述の先行技術に基づいて、本発明によると、前記目的は、
以下の組成(重量%で表示)
C: 0.08 〜 0.11%
Mn: 1.00 〜 1.30%
P: ≦ 0.030%
S: ≦ 0.004%
Si: 0.60 〜 0.80%
Al: ≦ 0.05%
N: ≦ 0.0060%
Cr: 0.30 〜 0.80%
Ti: 0.060〜 0.120%
残余鉄及び不可避の不純物
を有し、そして、複合相ミクロ組織(Komplexphasen-Gefuege)を形成する鋼を、厚さ1〜4mmを有する鋳造ストリップへ鋳造して;
900〜1100℃の範囲にある最終熱間圧延温度、20%を超える変形度で、前記鋳造ストリップを連続処理中にインラインで、0.5〜3.2mmの範囲にある厚さを有する熱間圧延ストリップへ熱間圧延して;
前記熱間圧延ストリップを、550〜620℃の範囲にある巻き取り温度で巻き取り;そして、
10%の最小破断伸びA80での、800MPaの最小引張強さRmを有する熱間圧延ストリップを得る;
フラット鋼生成物の製造方法によって達成される。
According to the present invention, based on the aforementioned prior art, the object is
The following composition (expressed in% by weight)
C: 0.08 to 0.11%
Mn: 1.00 to 1.30%
P: ≦ 0.030%
S: ≦ 0.004%
Si: 0.60 to 0.80%
Al: ≦ 0.05%
N: ≦ 0.0060%
Cr: 0.30 to 0.80%
Ti: 0.060 to 0.120%
Casting steel having residual iron and inevitable impurities and forming a composite phase microstructure (Komplexphasen-Gefuege) into a cast strip having a thickness of 1 to 4 mm;
Final hot rolling temperature in the range of 900-1100 ° C., hot deformation having a thickness in the range of 0.5-3.2 mm in-line during continuous processing of the cast strip at a degree of deformation greater than 20% Hot rolled into a rolling strip;
Winding the hot rolled strip at a winding temperature in the range of 550-620 ° C; and
With a minimum breaking elongation A 80 10% of, obtaining a hot rolled strip having a minimum tensile strength Rm of 800 MPa;
This is achieved by a method for producing a flat steel product.
本発明は、高張力で、包晶凝固する複合相鋼を熱間圧延ストリップへ加工するためのストリップ鋳造の可能性を利用する。この場合、鋳造ストリップそれ自体が小さい厚さを有しているので、自動車製造の分野で特に必要とされる厚さの小さいフラット生成物を製造するために、前記ストリップの熱間圧延の過程で比較的低い変形度のみを維持することが必要である。従って、本発明の方法によって、相当する鋳造ストリップの初めの厚さを特定することによって、熱間圧延ストリップを問題なく製造することが可能である。前記熱間圧延ストリップは、最適な特性分布での最大厚さ1.5mmを有し、そして、前記熱間圧延ストリップから、例えば、車両の支持体構造用の部品を製造することができる。 The present invention takes advantage of the possibility of strip casting to process high tension, peritectic solidified composite phase steel into hot rolled strips. In this case, the cast strip itself has a small thickness, so in the process of hot rolling of the strip to produce a thin product with a small thickness that is particularly required in the field of automobile production. It is necessary to maintain only a relatively low degree of deformation. Thus, by the method of the invention, it is possible to produce hot rolled strips without problems by specifying the initial thickness of the corresponding cast strip. The hot-rolled strip has a maximum thickness of 1.5 mm with an optimum distribution of properties, and parts from, for example, vehicle support structures can be produced from the hot-rolled strip.
熱間圧延間での変形度が低いために、このために必要とされる圧延力は、従来方法による熱間圧延スラブ又は薄スラブで必要とされる力よりも低く、その結果、幅の大きい熱間圧延ストリップ(従来方法で鋳造される同じ強度及び厚さを有する熱間圧延ストリップの幅よりも実質的に大きい)を、本発明の方法で問題なく製造することができる。従って、本発明によって、前記組成を有し、本発明により製造される複合相鋼からなり、そして、1200mmを超える(特に、1600mmを超える)幅を有する高張力熱間圧延ストリップを確実に製造することができる。 Due to the low degree of deformation during hot rolling, the rolling force required for this is lower than that required for hot rolling slabs or thin slabs according to conventional methods, and as a result is wider. Hot rolled strips (substantially larger than the width of hot rolled strips of the same strength and thickness cast by conventional methods) can be produced without problems with the method of the present invention. Therefore, according to the present invention, a high-strength hot-rolled strip having the above composition and made of the composite phase steel manufactured according to the present invention and having a width exceeding 1200 mm (especially exceeding 1600 mm) is reliably manufactured. be able to.
前記利点とは別に、本発明方法に特有のそれらの特徴及びプロセス変数(例えば、熱間圧延最終温度、冷却、巻取り温度)のために、本発明により構成されるタイプの高張力鋼を加工するためのストリップ鋳造工程の本発明の適用は、本発明により処理されるタイプの重要な鋼組成の確実な鋳造の可能性(さらに、それらの凝固態様について)を提供する。従って、ストリップの鋳造に特有な、鋳造ストリップの非常に素早い凝固によって、従来の製造と比較すると、中央溶解(Mittenseigerungen)の出現のリスクを実質的に減少させることができ、その結果、本発明により製造される熱間圧延ストリップは、その断面及びその長さにわたって特に均一な特徴分布及びミクロ組織を有する。 Apart from the advantages mentioned above, high strength steels of the type constructed according to the invention are processed because of their characteristics and process variables specific to the method of the invention (for example, hot rolling final temperature, cooling, winding temperature) The application of the present invention of the strip casting process to provide the possibility of reliable casting of important steel compositions of the type treated according to the present invention (and their solidification aspects). Thus, the very rapid solidification of the cast strip, which is characteristic of the casting of the strip, can substantially reduce the risk of the appearance of a central melt (Mittenseigerungen) compared to conventional production, so that the present invention The hot rolled strip produced has a particularly uniform feature distribution and microstructure across its cross section and its length.
本発明の方法の更なる特別な利点は、例えば、EP1072689B1に記載されるように、冷却中断の必要の結果としての、熱間圧延後と巻き取り後との間に維持されるべき、熱間圧延ストリップの特別な冷却サイクルを追加することなく、本発明により製造される熱間圧延ストリップが、少なくとも800MPaの高い強度を有することである。本発明の方法を実施する場合には、熱間圧延を比較的厳密に限定される温度枠で終了すること、そして、巻取りを正確に規定された温度範囲で実施すること、だけが保証される必要がある。単一工程の冷却がその合間に実施される。 A further special advantage of the method according to the invention is that the hot to be maintained between hot rolling and after winding as a result of the need for a cooling interruption, as described for example in EP 1072689 B1. Without adding a special cooling cycle of the rolled strip, the hot rolled strip produced according to the present invention has a high strength of at least 800 MPa. When carrying out the method of the invention, it is only guaranteed that the hot rolling is terminated in a relatively strictly limited temperature window and that the winding is carried out in a precisely defined temperature range. It is necessary to Single step cooling is performed in between.
本発明の方法の更なる利点は、本発明により製造されるストリップの機械的特性の範囲における拡張を、冷却及び圧延条件を変化させることによって、単一の鋼分析に基づいて、達成することができることである。 A further advantage of the method of the invention is that an extension in the range of mechanical properties of the strip produced according to the invention can be achieved on the basis of a single steel analysis by changing the cooling and rolling conditions. It can be done.
本発明により製造される熱間圧延ストリップは、次の冷間圧延ストリップへの加工に特に適当である。従って、本発明の或る実際の実施態様では、熱間圧延ストリップが提供され、前記熱間圧延ストリップは、自動車車体製造用に必要とされる、厚さ0.5〜1.4mm(特に、0.7mm〜1.3mmまで)を有する冷間圧延ストリップへ冷間圧延される。冷間圧延の間で生じる凝固を排除するために、冷間圧延ストリップを焼鈍温度750〜850℃で焼鈍することができる。この場合に、本発明の方法により製造される熱間圧延ストリップから製造される冷間圧延ストリップでは、最小引張強度800MPaを確実に保証することができる。同時に、冷間圧延ストリップの最小破断伸びA50は、10%である。 The hot-rolled strip produced according to the invention is particularly suitable for processing into the next cold-rolled strip. Accordingly, in one actual embodiment of the present invention, a hot rolled strip is provided, the hot rolled strip having a thickness of 0.5 to 1.4 mm (especially required for automobile body manufacturing) Cold rolled to a cold rolled strip having a thickness of 0.7 mm to 1.3 mm. To eliminate the solidification that occurs during cold rolling, the cold rolled strip can be annealed at an annealing temperature of 750-850 ° C. In this case, the minimum tensile strength of 800 MPa can be reliably ensured in the cold rolled strip manufactured from the hot rolled strip manufactured by the method of the present invention. At the same time, the minimum breaking elongation A 50 of the cold rolled strip is 10%.
本発明の更なる有利な実施態様によると、冷間圧延ストリップは、それ自体が公知である方法により、金属コーティング(例えば、これを亜鉛コーティングであることができる)を提供される。 According to a further advantageous embodiment of the invention, the cold-rolled strip is provided with a metal coating (for example it can be a zinc coating) by methods known per se.
本発明を、模範的な実施態様に基づいて、以下に詳しく説明する。 The invention is described in detail below on the basis of exemplary embodiments.
本発明の効果を実証するために実施される試験において、表1に示される組成を有する本発明により構成される2つの鋼A及びBを溶融し、双ロール鋳造機(Zweiwalzengiess-Maschine)で、1.6mm厚の鋳造ストリップへそれぞれ鋳造した。
ストリップを鋳造した後に、鋼A及びBから鋳造されたストリップを、最終熱間圧延温度WETで、1.25mmの厚さを有する熱間圧延ストリップへインラインに直接熱間圧延した。続いて、それぞれの場合において得られた熱間圧延ストリップを、冷却工程中で巻き取り温度HTまで冷却して巻き取った。巻き取り後に、鋼A及びBの各々から製造される熱間圧延ストリップは、それらの製造の間でそれぞれ維持される最終熱間温度WET及び巻き取り温度HTと共に表2に示される、引張強さRm及び破断伸びA80を有していた。
巻き取り及びピックリング後で、鋼Bから製造される熱間圧延ストリップを、0.7mm厚の冷間圧延ストリップへ冷間圧延して、800℃の焼鈍温度でインラインに焼鈍して、ストリップを再結晶化した。 After winding and pickling, the hot rolled strip produced from steel B is cold rolled into a 0.7 mm thick cold rolled strip and annealed inline at an annealing temperature of 800 ° C. Recrystallized.
15.4%の破断伸びA50での、この方法で得られる冷間圧延ストリップの引張強度Rmは、838MPaであった。 The tensile strength R m of the cold-rolled strip obtained in this way at a breaking elongation A 50 of 15.4% was 838 MPa.
Claims (9)
以下の組成(質量%で表示)
C: 0.08 〜 0.11%
Mn: 1.00 〜 1.30%
P: ≦ 0.030%
S: ≦ 0.004%
Si: 0.60 〜 0.80%
Al: ≦ 0.05%
N: ≦ 0.0060%
Cr: 0.30 〜 0.80%
Ti: 0.060〜 0.120%
残余鉄及び不可避の不純物
を有し、そして、複合相ミクロ組織を形成する鋼を、厚さ1〜4mmを有する鋳造ストリップへ鋳造して;
900〜1100℃の範囲にある最終熱間圧延温度、20%を超える変形度で、前記鋳造ストリップを連続処理中にインラインで、0.5〜3.2mmの範囲にある厚さを有する熱間圧延ストリップへ熱間圧延して;
前記熱間圧延ストリップを、550〜620℃の範囲にある巻き取り温度で巻き取り;そして、
10%以上の破断伸びA80 及び800MPa以上の引張強さRmを有する熱間圧延ストリップを得る;
前記製造方法。 A method for producing a flat steel product comprising:
Following composition (expressed in mass%)
C: 0.08 to 0.11%
Mn: 1.00 to 1.30%
P: ≦ 0.030%
S: ≦ 0.004%
Si: 0.60 to 0.80%
Al: ≦ 0.05%
N: ≦ 0.0060%
Cr: 0.30 to 0.80%
Ti: 0.060 to 0.120%
Casting steel having residual iron and inevitable impurities and forming a composite phase microstructure into a cast strip having a thickness of 1-4 mm;
Final hot rolling temperature in the range of 900-1100 ° C., hot deformation having a thickness in the range of 0.5-3.2 mm in-line during continuous processing of the cast strip at a degree of deformation greater than 20% Hot rolled into a rolling strip;
Winding the hot rolled strip at a winding temperature in the range of 550-620 ° C; and
Obtaining a hot rolled strip having 10% or more of elongation at break A 80 and 800MPa or more tensile strength Rm;
The manufacturing method.
Applications Claiming Priority (3)
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EP06123134.6 | 2006-10-30 | ||
EP06123134A EP1918402B1 (en) | 2006-10-30 | 2006-10-30 | Process for manufacturing steel flat products from a steel forming a complex phase structure |
PCT/EP2007/061388 WO2008052917A1 (en) | 2006-10-30 | 2007-10-24 | Method for manufacturing flat steel products from a steel forming a complex phase structure |
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US (1) | US20090277546A1 (en) |
EP (1) | EP1918402B1 (en) |
JP (1) | JP5232793B2 (en) |
KR (1) | KR101458039B1 (en) |
CN (1) | CN101528969B (en) |
AT (1) | ATE432372T1 (en) |
DE (1) | DE502006003830D1 (en) |
ES (1) | ES2325960T3 (en) |
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WO2009048838A1 (en) | 2007-10-10 | 2009-04-16 | Nucor Corporation | Complex metallographic structured steel and method of manufacturing same |
US20110277886A1 (en) | 2010-02-20 | 2011-11-17 | Nucor Corporation | Nitriding of niobium steel and product made thereby |
CN101928875A (en) * | 2009-06-22 | 2010-12-29 | 鞍钢股份有限公司 | High-strength cold-rolled plate with favorable forming property and preparation method thereof |
CN102303212B (en) * | 2011-06-24 | 2013-04-10 | 成都申信达机械有限公司 | Process for manufacturing lining board of wet-spraying machine |
CN103302255B (en) * | 2012-03-14 | 2015-10-28 | 宝山钢铁股份有限公司 | A kind of thin strap continuous casting 700MPa level high-strength air corrosion-resistant steel manufacture method |
CN103305759B (en) * | 2012-03-14 | 2014-10-29 | 宝山钢铁股份有限公司 | Thin strip continuous casting 700MPa grade high-strength weather-resistant steel manufacturing method |
CN103305770B (en) * | 2012-03-14 | 2015-12-09 | 宝山钢铁股份有限公司 | A kind of manufacture method of thin strap continuous casting 550MPa level high-strength air corrosion-resistant steel band |
US10053757B2 (en) | 2012-08-03 | 2018-08-21 | Tata Steel Ijmuiden Bv | Process for producing hot-rolled steel strip |
US10415111B2 (en) * | 2014-04-30 | 2019-09-17 | Jfe Steel Corporation | High-strength steel sheet for containers and method for producing the same |
CN104480397B (en) * | 2014-12-19 | 2017-06-23 | 山东钢铁股份有限公司 | A kind of 700MPa grades of Hot Rolling Automobile structural steel and preparation method thereof |
JP6778943B2 (en) | 2014-12-19 | 2020-11-04 | ニューコア・コーポレーション | Hot-rolled lightweight martensite steel sheet and its manufacturing method |
DE102016202005A1 (en) * | 2016-02-10 | 2017-08-10 | Thyssenkrupp Ag | Commercial vehicle wheel and use |
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CZ6999A3 (en) * | 1996-07-12 | 1999-10-13 | Thyssen Stahl Ag | Hot rolled steel band and process for producing thereof |
DE19710125A1 (en) * | 1997-03-13 | 1998-09-17 | Krupp Ag Hoesch Krupp | Process for the production of a steel strip with high strength and good formability |
JP3931455B2 (en) * | 1998-11-25 | 2007-06-13 | Jfeスチール株式会社 | Steel plate for can and manufacturing method thereof |
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FR2798871B1 (en) * | 1999-09-24 | 2001-11-02 | Usinor | PROCESS FOR PRODUCING CARBON STEEL STRIPS, ESPECIALLY STEEL FOR PACKAGING, AND STRIPS THUS PRODUCED |
CN1107122C (en) * | 2000-02-29 | 2003-04-30 | 济南济钢设计院 | Austenic-bainite Malleable steel and its preparation |
AUPQ779900A0 (en) * | 2000-05-26 | 2000-06-22 | Bhp Steel (Jla) Pty Limited | Hot rolling thin strip |
ATE438470T1 (en) * | 2000-09-29 | 2009-08-15 | Nucor Corp | PRODUCTION OF THIN STEEL SHEET |
AUPR047900A0 (en) * | 2000-09-29 | 2000-10-26 | Bhp Steel (Jla) Pty Limited | A method of producing steel |
EP1327697A4 (en) * | 2000-10-19 | 2009-11-11 | Jfe Steel Corp | Zinc-plated steel sheet and method for preparation thereof, and method for manufacturing formed article by press working |
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DE10128544C2 (en) * | 2001-06-13 | 2003-06-05 | Thyssenkrupp Stahl Ag | High-strength, cold-workable sheet steel, process for its production and use of such a sheet |
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2006
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EP1918402A1 (en) | 2008-05-07 |
ATE432372T1 (en) | 2009-06-15 |
EP1918402B1 (en) | 2009-05-27 |
CN101528969B (en) | 2012-01-11 |
JP2010508433A (en) | 2010-03-18 |
KR20090090300A (en) | 2009-08-25 |
CN101528969A (en) | 2009-09-09 |
KR101458039B1 (en) | 2014-11-03 |
US20090277546A1 (en) | 2009-11-12 |
DE502006003830D1 (en) | 2009-07-09 |
WO2008052917A1 (en) | 2008-05-08 |
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PL1918402T3 (en) | 2009-10-30 |
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