WO2010016430A1 - High-strength cold-rolled steel sheet excellent in weldability and process for production of same - Google Patents

High-strength cold-rolled steel sheet excellent in weldability and process for production of same Download PDF

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Publication number
WO2010016430A1
WO2010016430A1 PCT/JP2009/063622 JP2009063622W WO2010016430A1 WO 2010016430 A1 WO2010016430 A1 WO 2010016430A1 JP 2009063622 W JP2009063622 W JP 2009063622W WO 2010016430 A1 WO2010016430 A1 WO 2010016430A1
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Prior art keywords
amount
steel sheet
rolled steel
rolled
strength cold
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PCT/JP2009/063622
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French (fr)
Japanese (ja)
Inventor
吉田裕美
齋藤勇人
横田毅
田中靖
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Ｊｆｅスチール株式会社
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Priority to MX2011000901A priority Critical patent/MX2011000901A/en
Priority to US13/057,573 priority patent/US20110290383A1/en
Priority to EP09804914.1A priority patent/EP2312007B1/en
Priority to CN200980131036.0A priority patent/CN102119234B/en
Priority to KR1020117002627A priority patent/KR101335826B1/en
Priority to CA2731843A priority patent/CA2731843C/en
Publication of WO2010016430A1 publication Critical patent/WO2010016430A1/en

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Classifications

    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • 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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
    • 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
    • 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
    • C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
    • 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

Definitions

  • the present invention relates to a rolled steel sheet having processing suitable for use in automobiles, ships, etc., and more particularly to a high-rolled steel sheet having a tensile TS of 440 Pa and its manufacturing method.
  • a board provided with is disclosed.
  • plasmac tends to form pigtails as the speed increases, making it difficult to increase the speed, that is, to improve productivity.
  • the challenge is to achieve faster contact by improving the plate.
  • the purpose of the present invention is to provide a steel sheet having a high melting point of 440 MPa and a method for manufacturing the same, which does not generate impingement even when plunging at a high speed and causes the addition of terradrank material.
  • the ping-bid can be further prevented.
  • the bright rolled steel sheet contains a species of mass, 0 00 005 to 0.008, or Se 0 005 to 0.0 and Te 0 005 0 0.
  • the Akeno rolled steel plate is a hot-pressed slurry having the above composition.
  • the mass means the amount of the component element.
  • the amount of C is less than 0,005, it will lead to an increase in the amount of gas and gas on the steelmaking floor. In addition, if the amount exceeds 0.005, machining will be induced. Therefore, the amount of C is between 0.005 and 0.005. In addition, the amount of C is set to 0.003 below.
  • the amount of S must be 0 ⁇ up. However, the amount of S is increased to 0 and the strength lance is damaged. Therefore, the amount of S is 0 ⁇ ⁇ 1 ⁇ 0. In addition, the 5 quantity is reduced by 0.7.
  • n is an element effective for increasing the steel. To obtain this effect, the Mn content needs to be increased. However, if the amount exceeds 2.5, there will be problems such as promoting the center deviation in the slab and converting it to a final product. Therefore, the amount of n is ⁇ 2.5. From the standpoint of preventing FeS formation, Mn is S-bonded to form nS, and when the amount is S for the purpose of forming nS, (n 55) (S 32) 00 may be satisfied. Preferable.
  • the P amount is an effective element for increasing the level of steel. In order to obtain such an effect, the P amount needs to be over 0.0. However, if the amount of P exceeds 0.2, it will cause not only the destruction of the H Z part and the maternalization, but also the deterioration. Therefore, the amount of P is 0 ⁇ 0 to 0 ⁇ 2 S 0 5
  • the amount of S exceeds 0 05, the mother's sex will be changed as in the case of P. Therefore, the amount of S decreased by 0.5, and it was reduced. As mentioned above, it is preferable to satisfy 55) 5 32) 100.
  • so A is reduced by a specific range. so amount exceeds 0 ⁇ 05, 0 increases, process, intervene It can be a point. Therefore, it shall be below so 0 ⁇ 0 5.
  • the amount of N exceeds 0,007. Therefore, the amount of N drops to 0007, but it is less.
  • T improves the effectiveness by forming C and N products.
  • the amount of T needs to be 0 ⁇ 0 or higher.
  • the amount of T is set to 0 0 0.
  • B improves sex when present in a state.
  • the amount of B needs to be over 0.0005.
  • the amount is set to 0.05 to 0.5. The reason why it is possible to prevent the formation of a high-speed plumping bead with 0 and 0 is not necessarily clear, but it is considered that the viscosity of the molten steel is optimized and the mobility of is improved.
  • the content of is as described above, the surface properties are likely to deteriorate. In order to prevent this, it is necessary to add N on 0.03. However, the amount of N is If it exceeds 0.5, it will be summed. Therefore, the amount of N is set to 0.03 to 0.5. In addition, it is preferable to satisfy 025XCN075Xu when N amount is N amount.
  • the species contain 0 0 ⁇ 0 025 0 0080 Se 0500 0 and Te 0500 0 C, for the following reasons.
  • the 0 amount needs to be over 0.0025. More preferred is 0.0000. However, if the amount exceeds 0.0000, the result will be summed, the number of continuous slab buoys will increase, the insertion of the slur surface will increase, and there will be an adverse effect of increasing the number of intervening plates.
  • the light phase may be a shift between the naphthalite and the italite phase, or a mixture of both.
  • the light phase is below 50 ° in order to secure TS of 40 Pa but to prevent the welding from being shortened.
  • the bright rolled steel sheet is a hot-rolled 680 slurry with the above composition.
  • C Rolld at a lower temperature, pickled, cold rolled at a pressure of 40.
  • recrystallize 700 850C From the viewpoint of recrystallization in minutes, it is preferable to keep the temperature above 750oC for 30 ° C or more.
  • a converter or electric steel is melted, continuously produced, and slurried.
  • hot rolling of a slab can be performed by a method of heating and rolling, a method of rolling without heating, a method of performing a heat treatment for a short time, or the like.
  • Inter-rolling can be done with the above-mentioned finishing degree according to a conventional method. It can be done even with continuous crystal. Skins for the purpose of surface preparation, plate shape, etc. can be performed. It is also possible to perform such processes as chemical formation and treatment.
  • the degree is 900. Finished to C, and equivalent processing was performed at 580C for 4mm. With this, the scale is removed, and 60 rolling is performed.
  • compositionist 60A, plasma gas 0 / 6L n, dos L, 20mm,
  • the distance of 3 m was kept constant, and the degree was changed by 0, 2, and 4, and the raw line (X) of the pig bid was investigated by changing the angle.

Abstract

Provided are a high-strength cold-rolled steel sheet which has a TS of 440MPa or above and excellent weldability and which neither forms humping beads even when subjected to high-speed plasma welding and nor brings about deterioration in the workability of a tailored blank, and a process for production of same.  A high-strength cold-rolled steel sheet which has a TS of 440MPa or above and excellent weldability, characterized by having a composition which contains by mass C: 0.0005 to 0.005%, Si: 0.1 to 1.0%, Mn: 1 to 2.5%, P: 0.01 to 0.2%, S: 0.015% or less, sol. Al: 0.05% or less, N: 0.007% or less, Ti: 0.01 to 0.1%, B: 0.0005 to 0.0020%, Cu: 0.05 to 0.5%, and Ni: 0.03 to 0.5% with the balance being Fe and unavoidable impurities and a ferrite single phase structure.

Description

に優れた 延鋼板およびそ 製 術分野  Excellent in rolled steel sheet and its manufacturing field
本 、 鉄道 両 自動車、 船舶などの に用 るのに適した加工 を兼ね備えた 延鋼板、 特に、 引張 TSが 44０ Pa 上 高 延鋼板およびその製 法に関する。  The present invention relates to a rolled steel sheet having processing suitable for use in automobiles, ships, etc., and more particularly to a high-rolled steel sheet having a tensile TS of 440 Pa and its manufacturing method.
プ セスにおける ス 術 歩によ り、 量を０・００3０ まで低減した が比較的安価に大量に 造できるよ になり それに T や Nb などの 化物 素を添加して優れた加工 を付与した わゆる F n e s a F ee) タイプ 延鋼板が自動車 品や電気 器部品などに広 られるよ にな て る。 そのため、 の F タ イプ 延鋼板が開発されており、 例えば、 特許 2 には、 T やNbを添加した F鋼に、 さ らに Bを添加して 性の 上を図 た加工 に極めて優れた冷延鋼板が提案されて る。 また、 特許 3に は、 T やNb を添加した F鋼に、 さ らに N を添加して優れた ウ The process has been reduced to 0.0030, but it has become possible to manufacture a large amount at a relatively low cost, and it has been given excellent processing by adding chemicals such as T and Nb. F nesa Fee) type steel sheet is now widely used in automobiles and electrical parts. For this reason, F-type rolled steel sheets have been developed.For example, in Patent 2, F steel with addition of T and Nb is further excellent in processing that improves the properties by adding B. Cold rolled steel sheets have been proposed. Patent 3 also describes an excellent steel by adding N to F steel added with T and Nb.
を付与した 板が開示されて る。  A board provided with is disclosed.
方、 近年、 自動車用鋼板にお ては、 車体の 量化や衝突 全性の 点 ら 度化が図られてお 、 また、 工程の や金型 の 減などを目 的に、 性が異なる 2 上 鋼板を 接して一体化したテ ラ ド ランク材が用 られるよ にな て る。 そのため、 優れた加工  On the other hand, in recent years, automotive steel sheets have been improved in terms of quantification of vehicle bodies and collision safety, and the characteristics are different in order to reduce the number of processes and molds. Teradlanc materials that come in contact with and integrate steel plates are now being used. Therefore, excellent processing
を兼ね備えた 、 特に、 TS が 44０ Pa 上の高 延鋼板に対 する要望が強 な て る。  In particular, there is a strong demand for high-rolled steel sheets with a TS of 440 Pa.
に関しては、 上記したよ F タイプの 延鋼板が望まれるが、 F タイプの 延鋼板を用 たテ ラ ドブランク材の溶 に ては、 ほ んど 討されて な 。 テ ラ ドブラ ク材の溶 に ては、 特 許 4に、 異なる 板を、 設備 が安価で、 高速 可能で、 も 料を使用しな プラ 接によ りテ ラ ドブラ ク材を製造 する方法にお て、 側 鋼板の 量を０・ 上にしたり、 S 量を０・ 8 上にして、 ピ グビ ド の 生を防止す る方法が提案されて る。 術文献As mentioned above, F-type steel sheets are desired as described above, but there has been little discussion about melting of terad blanks using F-type steel sheets. For melting the black brick material, patent 4 is a different plate, the equipment is inexpensive and high speed is possible. In the method of manufacturing terrad black materials by plastic contact without using metal, the amount of side steel plate is increased to 0 · or S content is increased to 0 · 8, and A method to prevent this has been proposed. Technical literature
6 246344 6 246344
2 1 49943 2 1 49943
3 2 232342 3 2 232342
4 2００3 94 7０ 報 発明の  4 200 3 94 70 Report Invented
明が解決しよ とする課題  Issues that Ming tries to solve
し しながら、 特許 4 に記載のテ ラ ド ラ ク材 製 法では 少な と も一方の 板の C量を０・ 上ある は S 量を０・ 8 上 する必要があり、 テ ラ ドブラ ク材の加 が著し ると 題がある。  However, in the terradrac material manufacturing method described in Patent 4, it is necessary to increase the amount of C on one plate to 0 or above, or to increase the amount of S to 0 or 8; There is a title when Noka is writing.
更に、 プラズ ア ク 、 度が速 なると ンピ グビ ドが 形成されやす なるため、 度の 速化 すなわち 産性の 善が難 し 題がある。 この 題に対して、 明では、 板を改善するこ によ り、 接の 速化を達成するこ を課題 する。  Furthermore, plasmac tends to form pigtails as the speed increases, making it difficult to increase the speed, that is, to improve productivity. In order to deal with this problem, the challenge is to achieve faster contact by improving the plate.
すなわち、 、 高速でプラズ 行 ても ンピ グビ ドが 発生 ず、 テ ラ ド ランク材の加 の 化を招 こと な TS が 44０MPa 上の溶 に優れた 延鋼板およびその製 法を提供する こ を目的とする。  In other words, the purpose of the present invention is to provide a steel sheet having a high melting point of 440 MPa and a method for manufacturing the same, which does not generate impingement even when plunging at a high speed and causes the addition of terradrank material. And
題を解決するための  To solve the problem
らは、 プラ 接の 速化を行 ても ンピングビ ドが発生 せず、 テ ラ ドブランク材の加 の 化を招 こ のな TS が 44０ Pa 上の高 延鋼板の に て 討を行 た結果、 以下の 見を見出した。 F鋼に を添加することで高速プラ ンピ グビ ド 生 を抑制し、 さ らに適切な 囲に ０量を規定するこ により高速プラ Et al. Reported that TS does not generate bumping even when the speed of plastic contact is increased, and that TS increases the thickness of the terad blank, and as a result of the discussion on the high-rolled steel sheet at 440 Pa. I found the following observations. By adding to F steel, high-speed plumbing is suppressed, and by specifying 0 amount in an appropriate range, high-speed plastic
ピングビ ドの 生をより そ 防止できる。 The ping-bid can be further prevented.
) C量を０・ ００5 下とし、 T を添加して F とし、 ライ ト 相 織にすることによ りテ ラ ド ランク と しても優れた加工 が 得られる。  ) By making the amount of C below 0.005, adding T to F, and making it a light phase weave, excellent processing can be obtained even with a terrad rank.
、 以上の知見に基 きなされたもので、 質量 、 C ０ ００5 ０ ０ ０5 ０ ０ ～2 5 P ０ ０ 2 S ０ ０ 5 So ０ 5 N ０ ０7 T ０ ～０ B ０ ００5 ０ ００2０ C ０ ０5 ０ 5 N ０ ０3 ０ 5 含有し、 残部 Feおよび不可避的 ・ らなる 成を有し、 か ライ ト 相 らなる 織を有するこ を特徴 する T が 44０ Pa 上の溶 に優れた 延鋼板を提供する。  Based on the above knowledge, mass, C 0 005 0 0 05 0 0 to 2 5 P 0 0 2 S 0 0 5 So 0 5 N 0 07 T 0 to 0 B 0 00 0 00 20 C 0 A rolled steel sheet having a melting point of over 440 Pa, characterized by having a woven structure consisting of a lime phase and a woven structure consisting of the remaining Fe and inevitable composition. provide.
明の 延鋼板は、 に、 質量 、 ０ ０ ００25～０・００8０ 、 ま たは Se ０ ００5～０・０ および Te ０ ００5 ０ ０ ちの な と も 種 を含有するこ が好まし 。  It is preferable that the bright rolled steel sheet contains a species of mass, 0 00 005 to 0.008, or Se 0 005 to 0.0 and Te 0 005 0 0.
明 延鋼板は、 上記のよ な組成を有するスラ を、 熱間圧 。  The Akeno rolled steel plate is a hot-pressed slurry having the above composition.
延 、 68０C 下の 度で巻 、 酸洗 、 圧 4０ 上で冷 圧延 引続き 7００～ 。Rolled at a temperature below 680C, pickled, cold rolled at a pressure of 40, and continued at 700-.
85０Cの 囲で再結晶 施す方法によ り製造できる。 明の  Manufactured by recrystallization in the range of 850C. Mysterious
明によ り、 プラズ 接の 速化を行 ても ンピングビ ドが発生 せず、 テ ラ ドブランク材の加 の 化を招 こ のな TS が 44０ Pa 上の溶 に優れた 延鋼板を製造できるよ にな た。 また、 明の 延鋼板は、 優れた加工 を備えて るため、 自動車 品の みならず 器部品などにも好適である。 明を実施するための 良の  As a result, it is possible to produce a steel plate with excellent melting at a TS of 440 Pa, which does not generate bumping even if the blast contact speed is increased, and does not lead to the addition of the terad blank material. It became. In addition, Akira rolled steel sheets are suitable not only for automobile parts but also for equipment parts because they have excellent processing. Good for carrying out Ming
下に、 明の 細を説明する。 なお、 成分 素の量を表す 、 特に断 らな 限り質量 意味する。  Below, I will explain the details. In addition, unless otherwise indicated, the mass means the amount of the component element.
1)  1)
０ ０００5 ０ ００5 C量が ０ ０００5 満だ 、 製鋼 階で の 高 なり ガスな ス ト増も招 。 また、 量が ０・００5 超えると加工 の 化を 招 。 したが て、 C量は０・０００5～０・００5 する。 まし は、 C量を０・０ ０3 下とする。 0 005 0 005 If the amount of C is less than 0,005, it will lead to an increase in the amount of gas and gas on the steelmaking floor. In addition, if the amount exceeds 0.005, machining will be induced. Therefore, the amount of C is between 0.005 and 0.005. In addition, the amount of C is set to 0.003 below.
S ０ ０  S 0 0
は、 鋼の高 度化に有効な 素である。 そ した効果を得るには、 S 量 は０・ 上とする必要がある。 し しながら、 S 量が ・０ 超える ライ ト 化を招き、 強度 ランスを損な 。 したが て、 S 量は０・ ～1・０ する。 まし は、 5 量を０・ 7 下 する。  Is an effective element for improving the steel. In order to obtain this effect, the amount of S must be 0 · up. However, the amount of S is increased to 0 and the strength lance is damaged. Therefore, the amount of S is 0 · ~ 1 · 0. In addition, the 5 quantity is reduced by 0.7.
Mn 2 5 Mn 2 5
nは、 鋼の高 度化に有効な 素である。 そ した効果を得るには、 Mn量 は 上とする必要がある。 し しながら、 量が 2・ 5 超える と、 スラ ブ中の中心偏 助長したり、 最終 品の 化さ るなどの 題が ある。 したが て、 n量は ～2・ 5 する。 なお、 FeS 成による 性 を防止する観点 ら、 Mn は の S 結合し、 nS を形成さ る 目的で 量を 、 S量を したとき、 ( n 55) ( S 32) ００ を満足さ ることが好まし 。  n is an element effective for increasing the steel. To obtain this effect, the Mn content needs to be increased. However, if the amount exceeds 2.5, there will be problems such as promoting the center deviation in the slab and converting it to a final product. Therefore, the amount of n is ~ 2.5. From the standpoint of preventing FeS formation, Mn is S-bonded to form nS, and when the amount is S for the purpose of forming nS, (n 55) (S 32) 00 may be satisfied. Preferable.
P ０ ０ ０ 2  P 0 0 0 2
Pは、 鋼の高 度化に有効な 素である。 そ した効果を得るには、 P量は ０・０ 上とする必要がある。 し しながら、 P量が ０・ 2 超えると H Z部 における 壊の 念や母 性の 化を招 のみならず して の 化を招 。 したが て、 P 量は ０・０ ～０・ 2 する S ０ 5  P is an effective element for increasing the level of steel. In order to obtain such an effect, the P amount needs to be over 0.0. However, if the amount of P exceeds 0.2, it will cause not only the destruction of the H Z part and the maternalization, but also the deterioration. Therefore, the amount of P is 0 · 0 to 0 · 2 S 0 5
S量が ０ ０ 5 超える と、 P 同様、 母 の 性の 化を招 。 したが て、 S量は０・０ 5 下 し、 少な ほど まし 。 なお、 上記 のよ に、 55) 5 32) 1００を満足させるこ が好まし 。  If the amount of S exceeds 0 05, the mother's sex will be changed as in the case of P. Therefore, the amount of S decreased by 0.5, and it was reduced. As mentioned above, it is preferable to satisfy 55) 5 32) 100.
so A ０ ０5  so A 0 05
は通常 階での 素 して利用されるが、 明では、 酸素を 特定 囲に ト するため、 so A 量は０・０5 下 する。 so 量が０・ ０5 超える 、 ０ が多 なり 、 加工 化させる 、 介在 れ 点となり得るなど まし な 。 したが て、 so ０・０ 5 下とする。 Is normally used as an element in the first floor, but in order to reduce oxygen to 0.50, the amount of so A is reduced by a specific range. so amount exceeds 0 · 05, 0 increases, process, intervene It can be a point. Therefore, it shall be below so 0 · 0 5.
N ０ ００7  N 0 007
N量が ０ ００7 超える 加工 効性の 化を招 。 したが て、 N 量は０ ００7 下 するが、 少な ほど まし 。  The amount of N exceeds 0,007. Therefore, the amount of N drops to 0007, but it is less.
T ０ ０ ０  T 0 0 0
T は CやN 出物を形成して 効性を向上さ る。 そ し た効果を得るには、 T 量は０・ ０ 上とする必要がある。 し しながら、 T 量が ０・ 超える 、 合金 ス トの 加をもたらす。 したが て、 T 量は ０ ０ ０ とする。 なお、 次に述 る Bの 果を有効に発揮さ るには、 T 量 を T 、 N量を N した き、 N 4 48) T ０を満足させることが 好まし 。  T improves the effectiveness by forming C and N products. In order to obtain this effect, the amount of T needs to be 0 · 0 or higher. However, when the amount of T exceeds 0 ·, it results in the addition of alloy stock. Therefore, the amount of T is set to 0 0 0. In order to effectively demonstrate the results of B described below, it is preferable to satisfy N 448) T 0 when the T amount is T and the N amount is N.
B ０ ０００5 ０ ００2０  B 0 005 0 00 20
Bは、 態で存在すると 性を向上さ る。 した効果を 得るには、 B量は０・０００5 上とする必要がある。 し しながら、 B量が ０ ０ ０2０ 超える れを助長する。 したが て、 B量は０ ０００5 ０ ００2０ とする。  B improves sex when present in a state. In order to obtain the effect, the amount of B needs to be over 0.0005. However, it encourages the amount of B to exceed 0 0 0 20. Therefore, the amount of B is set to 0 005 0 002.
０ 5 ０ 5  0 5 0 5
は、 加工 化さ ずに 度化を図れる と もに、 高速プラ  Can be refined without machining, and high-speed plastic
ンピングビ ドの 生を防止するのに効果的な 素である。 特に、 後述する範囲の ０ との で効果が高まる。 そ した効果を得るには 量は０・０5 上 する必要がある。  It is an effective element for preventing the generation of bumping bids. In particular, the effect increases with 0 in the range described later. To get that effect, the amount needs to be increased by 0.05.
し しながら、 量が ０・ 5 超える その 和すると もに、 表面性 状の し 化を招 。 したが て、 量は０・０5～０・ 5 とする。 なお、 と 0 の で高速プラズ ンピングビ ドの 生を防止でき る理由は 必ずしも明確ではな が、 に溶融した鋼の粘性が適正化さ れ、 の 動性が改善されるため 考えられる。  However, when the amount exceeds 0.5, the surface texture becomes distorted. Therefore, the amount is set to 0.05 to 0.5. The reason why it is possible to prevent the formation of a high-speed plumping bead with 0 and 0 is not necessarily clear, but it is considered that the viscosity of the molten steel is optimized and the mobility of is improved.
N ０ 3 ０ 5  N 0 3 0 5
の 有量を上記のよ にする と、 表面性状が悪化しやす なる。 それを 防ぐ 的で、 ０・０3 上の N を添加する必要がある。 しかしながら、 N 量が ０・ 5 を超えるとその 和する。 したが て、 N 量は０・０3～０・ 5 とす る。 なお、 N 量を N 量を したとき、 ０ 25X C N ０ 7 5 X u を満足させることが好まし 。If the content of is as described above, the surface properties are likely to deteriorate. In order to prevent this, it is necessary to add N on 0.03. However, the amount of N is If it exceeds 0.5, it will be summed. Therefore, the amount of N is set to 0.03 to 0.5. In addition, it is preferable to satisfy 025XCN075Xu when N amount is N amount.
Feおよび不可避的 であるが、 さ らに、 以下 由で、 ０ ０・０ ０25 ０ ００8０ Se ０００5 ０ ０ および Te ０００5 ０ ０ C ち な も 種が含有されることが好まし 。  In addition to Fe and unavoidable, it is also preferred that the species contain 0 0 · 0 025 0 0080 Se 0500 0 and Te 0500 0 C, for the following reasons.
０ ０ ００25 ０ ００8０  0 0 0025 0 0080
述したよ に、 との で高速プラズ ピングビ ド の 生をさ らに抑制できる。 との 、 おそら 溶接 の の  As mentioned above, the generation of high-speed plapping bid can be further suppressed with and. Of the welding of
力がさらに適正化 れたものと考えられる。 そ した効果を得る には、 0量は０・００25 上とする必要がある。 よ り好まし は、 ０・００4 ０ 上 する。 し しながら、 その量が ０・００8０ 超えると、 その 果が 和する 、 連続 スラブ ブ ホ が多 なり スラ 面の 入れ ス トが増大したり 、 介在 が増加して 板の 化さ る悪影響が出 る。  It is thought that the power was further optimized. In order to obtain such an effect, the 0 amount needs to be over 0.0025. More preferred is 0.0000. However, if the amount exceeds 0.0000, the result will be summed, the number of continuous slab buoys will increase, the insertion of the slur surface will increase, and there will be an adverse effect of increasing the number of intervening plates. The
Se ０ ０００5 ０ ０ Te ０００5 ０ Se 0 005 0 0 Te 0 000 0
e Teは、 0 同様に、 との ・ 力を 適正化し、 高速プラ ピングビ ドの 生を防止する。 そ した効果を得るには、 SeやTe量は０・０００5 上とする必要がある。 し し ながら、 SeやTe量が 0・０ 超える その 和する。  e Te, just like 0, optimizes the force with and prevents high-speed plumbing. In order to obtain such an effect, the amount of Se or Te must be over 0.005. However, the amount of Se and Te exceeds 0 · 0.
2)  2)
の 点 ら、 ライ ト 相の 織 する必要がある。 ここで、 ライ ト 相とは ナ フ ライ ト 、 イ チック ライ ト相の ずれでもよ 、 両者が混在して てもよ 。 なお、 4０ Paの TSを確保する もに溶接 の 端な 化を防止するため、 ライ ト相の平 5０ 下であるこ が好まし 。  From this point, it is necessary to weave the light phase. Here, the light phase may be a shift between the naphthalite and the italite phase, or a mixture of both. In addition, it is preferable that the light phase is below 50 ° in order to secure TS of 40 Pa but to prevent the welding from being shortened.
3)  3)
明の 延鋼板は、 上記のよ な組成を有するスラ を、 熱間圧 延 、 68０。C 下の 度で巻 、 酸洗 、 圧 4０ 上で冷 圧延 。  The bright rolled steel sheet is a hot-rolled 680 slurry with the above composition. C Rolled at a lower temperature, pickled, cold rolled at a pressure of 40.
引続き 7００ 85０Cの 囲で再結晶 施す方法によ り製造できる。 間圧延 の 68０。CSubsequently, it can be produced by a method of recrystallization in the range of 7000850C. 680 for hot rolling. C
6 。  6.
度が 8０Cを超えると FeやT などと Pの 合物ができやす 、 そ の後の冷間圧延 に深 に好まし 織の 達を阻 害す 。  When the temperature exceeds 80C, it is easy to form a mixture of Fe, T, etc. with P, and it is deeply preferred for the subsequent cold rolling, which prevents the weaving.
る。 したが て、 68０C 下 する。 よ り好まし は 65０3 下とする。  The Therefore, it goes down to 680C. More preferred is below 6503.
圧延の 4０ 上  40 above rolling
点から、 4０ 上とする。 、 と に り性向上 の観点 らは 5０ 上とすることが好まし 。  From the point, it is 40 above. From the viewpoint of improving performance, it is preferable to set the value above 50.
結晶 7００ 85０で  Crystal 700
再結晶さ るために、 焼鈍 7００。C 上とする必要があるが、 85０。Cを 超える ライ ト粒が 、 強度低下や表面 状の 化を招 。 した 。  Annealing 700 to recrystallize. C needs to be above 850. Light grains exceeding C lead to strength reduction and surface modification. did .
が て、 再結晶 7００ 85０C する。 分に再結晶さ る観点 ら は、 75０oC 上の温 3０ 以上保持するこ が好まし 。 Then recrystallize 700 850C. From the viewpoint of recrystallization in minutes, it is preferable to keep the temperature above 750oC for 30 ° C or more.
そ 他の製 、 通常の 法を適用できる。 すなわち、 転炉または電 気 鋼を溶製し、 連続 造してスラ する。 また、 スラブを熱間圧延す るには、 加熱 延する方法、 加熱することな 延する方法、 短時間 加熱処理を施して 延する方法などで行える。 間圧延は、 常法にしたが て 以上の仕上 度で圧延すればよ 。 結晶 、 、 連 続 ずれでも行える。 、 表面 整、 板 状の 化な どを目的にしたスキン ス 行える。 また、 その 、 化成 理、 め き 理などの 理を施すこと も可能である。 に示す 、 ０、 Seを含有する基本組成０・ ００2 ０ 8 n ０・ ０ 5 P ０ ００5 S ０ ０2 so ０ ００3 N ０ ０4 T ０ ００ ０ B Dg No 7を 真空 製し、 2００でで h 、 粗 行 て 35mmの ト を作製した。 この ト を 125０。Cで h 、 7 で最終 。  Other manufacturing and normal methods can be applied. In other words, a converter or electric steel is melted, continuously produced, and slurried. In addition, hot rolling of a slab can be performed by a method of heating and rolling, a method of rolling without heating, a method of performing a heat treatment for a short time, or the like. Inter-rolling can be done with the above-mentioned finishing degree according to a conventional method. It can be done even with continuous crystal. Skins for the purpose of surface preparation, plate shape, etc. can be performed. It is also possible to perform such processes as chemical formation and treatment. The basic composition containing 0, Se, 0, 002 0 8 n 0, 0 5 P 0 005 S 0 02 so 0 003 N 0 04 T 0 00 0 B Dg No 7 is made in vacuum, and at 2000, h Roughly, a 35mm G was produced. This is 1250. H for C, 7 for final.
度が 9００。Cとなるよ に仕上 行 、 58０Cで h の り相 当 処理を行 て 4mmの と した。 この によ てスケ 去し、 6０ 圧延を行 て ・ 6m の し、 ソ ト 。  The degree is 900. Finished to C, and equivalent processing was performed at 580C for 4mm. With this, the scale is removed, and 60 rolling is performed.
スを用 て 83０Cで 8０s。c ０CC secの 度で冷却する再結 行 、 で 板表面に付着したソ トを除去するための 行 たのち、 伸張 ０・ 5 スキン ス 施した。 80s at 830C. c Re-cooling at 0CC sec After removing the sticking to the surface of the board with a line, stretched 0.5 skins.
そして、 同一組成 士を、 6０A、 プラズ ガス ０・ 6L n、 ド ス L 、 ノ 2 ０mm 、 ノ  And the same compositionist, 60A, plasma gas 0 / 6L n, dos L, 20mm,
距離 3 mの 件を一定にし、 度を０・ 2 ・ 4 で変えてプ ラズ 行 、 ピ グビ ドの 生 (X) を調査した。  The distance of 3 m was kept constant, and the degree was changed by 0, 2, and 4, and the raw line (X) of the pig bid was investigated by changing the angle.
果を表 示す。  Display the results.
来 プラズ 接では ンピングビ ドを発生 ずに溶接できる限界 度が ０・ ０ 4 m 度であ たのに対し、 明である を含有する No 3)は、 m の 速な溶接 度にしても、 さ らに 0や 。を含有す る N ・ 4～7)は、 m m n 上の高速な溶接 度にしても ンピ グビ ドが発生 ず、 高速プラ に優れて ることがわ る。 While the limit of welding that can be welded without the occurrence of an impinging bead was 0.04 m degrees, the No. 3) containing clear is not necessary even with a rapid welding degree of m. Also 0 or. N · 4 to 7) containing Ng does not generate nigpibid even at a high welding degree on mmn, indicating that it is excellent for high-speed plastic.
Figure imgf000010_0001
2
Figure imgf000010_0001
2
2に示す 成の No・ ～Fを 製し、 連続 造により スラ とした 。  The products No. to F shown in Fig. 2 were manufactured and made into slurries by continuous production.
後、 2００。Cで加熱 、 9００ の 上 度で 上 行 、 58０Cの 度 で巻 て、 6mm 4mmの した。 この 、 圧 6０ 圧延を行って 2 。  Later, 200. Heated at C, ascending at 990 ° C, wound at 580 ° C, 6mm 4mm. This is a 60 roll.
・ 4 ・ 6m の とし、 焼鈍 83０C で連続 鈍し、 伸張 ０・ 5 スキン ス 施した。  ・ It was 4 ・ 6m, and it was blunted continuously at 830C, and stretched 0.5 skins.
そして、 同一組成の 、 3に示す板 の 合わ で、  And the combination of the plates shown in 3 with the same composition,
6０ 、 プラ ガス ０ 6L 、 ド ガス L m ノ 2・０ 、 ノ 距離 3m 、 nの 件でプ ラズ 行 、 ンピングビ ドの 生の X) ( )を調査した。 ま た、 得られた 板の 向に直角な方向 TS E 、 および 値を J S 5 を用 て調査した。  In the case of 60, Plagas 06L, Degas Lm No 2.0, No Distance 3m, n, the plastic line, and the raw X) () were investigated. In addition, the direction TSE and the value perpendicular to the direction of the obtained plate were investigated using JS5.
果を表3に示す。 成を有する 、 44０ Pa 上の T S が得られ、 加工 にも優れ、 高速プラ ンピングビ ドが発生 しな こ がわ る。 The results are shown in Table 3. A TS of 440 Pa can be obtained, and it is excellent in processing, so that a high-speed plumbing bid does not occur.
Figure imgf000011_0001
Figure imgf000011_0001

Claims

求の C ０ ０００5 ０ ００5 S ０ ０ 2 5 P ０ ０ ０ 2 S ０ ０ 5 So A ０5 N ０ ０7 T ０ ０ ０ B ０ ００5 ０ ０2０ C ０ 5～０ N ０ 3～０ 5 含有し、 残部 Feおよび不可避的 物 らなる 成を有し、 ライ ト 相 ら なる 織を有することを特徴 する引張 度が 44０ Pa 上 溶 に優れた 延鋼板。 2・ にお て、 さらに、 質量 ０ ０ ０25～０・００8０ 含有す る 成を有することを特徴とする引張 度が 44０MPa 上の溶 に優れた 延鋼板。 3 または 2にお て、 さ らに、 質量 、 Se ０ ００5 ０・０ よびTe ０ ００5～０ ０ ちの な とも 種を含有する 成を有するこ とを特徴とする引張 度が 44０MP 上の溶 に優れた 延鋼板。 4・ ～3の ずれ 項に記載の 成を有するスラブを、 熱間圧延 、 68０で以下の 度で巻 、 酸洗 、 圧 4０ 上で冷 圧延 、 引続き 7００～85０。Cの 囲で再結晶 施すこ を特徴とする引張 度 が 44０ Pa 上の溶 に優れた 延鋼板の 。  C 0 005 0 005 S 0 0 2 5 P 0 0 0 2 S 0 0 5 So A 05 N 0 07 T 0 0 0 B 0 005 0 020 C 0 5 to 0 N 0 3 to 0 5 A rolled steel sheet having a balance of Fe and an inevitable material and having a weave of a light phase and excellent tensile strength of 440 Pa. 2. A rolled steel sheet excellent in melting at a tensile strength of 440 MPa, characterized by having a composition further containing a mass of 0.025 to 0.0000. In addition, the tensile strength of 440MP is characterized by having a composition containing a seed of any of 3 or 2, Se 0 005 0 · 0 and Te 0 005 to 0 0. Excellent rolled steel sheet. The slab having the composition described in 4 · to 3 is hot-rolled, wound at 680 at the following degrees, pickled, cold-rolled on a pressure of 40, and continuously from 700 to 850. A steel sheet with excellent tensile strength at 440 Pa, characterized by recrystallization within C.
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TWI506146B (en) 2015-11-01
EP2312007A4 (en) 2012-08-01
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CN102119234A (en) 2011-07-06
KR101335826B1 (en) 2013-12-03
US20110290383A1 (en) 2011-12-01
EP2312007A1 (en) 2011-04-20
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TW201402833A (en) 2014-01-16
CA2731843A1 (en) 2010-02-11
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CA2731843C (en) 2014-10-28
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