JP2015503023A - Steel plate for warm press forming, warm press forming member, and manufacturing method thereof - Google Patents

Steel plate for warm press forming, warm press forming member, and manufacturing method thereof Download PDF

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JP2015503023A
JP2015503023A JP2014539881A JP2014539881A JP2015503023A JP 2015503023 A JP2015503023 A JP 2015503023A JP 2014539881 A JP2014539881 A JP 2014539881A JP 2014539881 A JP2014539881 A JP 2014539881A JP 2015503023 A JP2015503023 A JP 2015503023A
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warm press
steel plate
press forming
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JP6043801B2 (en
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ジン−クン オー、
ジン−クン オー、
キョ−ヨン イ、
キョ−ヨン イ、
ヨル−レ チョー、
ヨル−レ チョー、
ウル−ヨン チェ、
ウル−ヨン チェ、
キ−ス キム、
キ−ス キム、
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Posco Co Ltd
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Posco Co Ltd
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    • B—PERFORMING OPERATIONS; TRANSPORTING
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    • B21B—ROLLING OF METAL
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    • B21B1/02—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling heavy work, e.g. ingots, slabs, blooms, or billets, in which the cross-sectional form is unimportant ; Rolling combined with forging or pressing
    • B21B1/04—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling heavy work, e.g. ingots, slabs, blooms, or billets, in which the cross-sectional form is unimportant ; Rolling combined with forging or pressing in a continuous process
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Abstract

本発明は、温間プレス成形によって高い強度を有するとともに、優れた延伸率を確保して衝突特性に優れた温間プレス成形用鋼板及びこれを用いた温間プレス成形部材を提供するもので、重量％で、Ｃ：０．０１〜０．５％、Ｓｉ：３．０％以下（０は除く）、Ｍｎ：３〜１５％、Ｐ：０．０００１〜０．１％、Ｓ：０．０００１〜０．０３％、Ａｌ：３．０％以下（０は除く）、Ｎ：０．０３％以下（０は除く）、Ｆｅ及び不可避な不純物を含む温間プレス成形用鋼板、これを用いた温間プレス成形部材、及びこれらの製造方法を提供する。The present invention provides a hot press-formed steel sheet having a high strength by warm press molding, ensuring an excellent stretch ratio and excellent impact characteristics, and a warm press-formed member using the same. C: 0.01 to 0.5%, Si: 3.0% or less (excluding 0), Mn: 3 to 15%, P: 0.0001 to 0.1%, S: 0.005% by weight. 0001 to 0.03%, Al: 3.0% or less (excluding 0), N: 0.03% or less (excluding 0), steel plate for warm press forming containing Fe and inevitable impurities, and using this A warm press-formed member and a method for manufacturing the same are provided.

Description

本発明は、自動車構造部材または補強材に用いられる鋼板であって、より詳細には、温間プレス成形後に高い強度を有するとともに優れた延伸率を確保することにより、衝突吸収能及びめっき材の耐食性を向上させることができる温間プレス成形用鋼板、これを用いた温間プレス成形部材、及びこれらの製造方法に関する。   The present invention is a steel plate used for an automobile structural member or a reinforcing material, and more specifically, has a high strength after warm press forming and secures an excellent stretch ratio, thereby improving the impact absorption capacity and the plating material. The present invention relates to a steel plate for warm press forming that can improve corrosion resistance, a warm press formed member using the same, and a method for producing them.

最近の自動車産業では、環境に優しい燃費及び乗客の安全性規制に準じた耐衝突性向上へのニーズが高まっている。このため、車体の高強度化による自動車軽量化及び耐衝突性の向上に対する研究及び適用が活発に行われている。   In the recent automobile industry, there is a growing need for improving impact resistance in accordance with environmentally friendly fuel consumption and passenger safety regulations. For this reason, research and application are being actively conducted to reduce the weight of automobiles and improve collision resistance by increasing the strength of the vehicle body.

このようなニーズに対応すべく、高い強度を有しながらも、優れた成形性を確保し、形状の制御能力に優れた方法として熱間成形方法が提示されている。このような方法は特許文献１及び２などで提案されている。上記のような方法は、熱処理前の低い強度及び高い加工性を用いてオーステナイト単相域において熱処理及びプレス成形を行い、金型による急冷を施すことにより、最終製品において主相をマルテンサイトにする、超高強度鋼板を得る製造方法である。   In order to meet such needs, a hot forming method has been proposed as a method which has excellent strength while maintaining high strength and has excellent shape control ability. Such a method is proposed in Patent Documents 1 and 2 and the like. In the above method, the main phase in the final product is martensite by performing heat treatment and press molding in the austenite single phase region using low strength and high workability before heat treatment, and quenching with a mold. This is a production method for obtaining an ultra-high strength steel sheet.

しかし、上記技術では、オーステナイト単相域の高い加熱温度により、非めっき材の場合、製造後に生じた表面の酸化スケールを除去する必要があり、高い温度を確保するために多くの費用が求められる。   However, in the above technique, it is necessary to remove the oxidized scale of the surface generated after the production in the case of a non-plated material due to the high heating temperature of the austenite single phase region, and a large amount of cost is required to ensure a high temperature. .

また、Ｚｎめっき材またはＡｌめっき材の場合、めっき材の揮発またはロール癒着が発生して生産性を低下させる可能性がある。Ｚｎの融点は５００℃以下、Ａｌの融点も７００℃を超えないことから、上記のように高温で熱処理を行うと、ＺｎまたはＡｌが一部融解するようになるため、めっき材としての特性を確保することが困難になり、ＺｎまたはＡｌが加工時に成形枠に融着して成形に悪影響を及ぼすという問題がある。   Further, in the case of a Zn plating material or an Al plating material, volatilization of the plating material or roll adhesion may occur and productivity may be reduced. Since the melting point of Zn is 500 ° C. or less and the melting point of Al does not exceed 700 ° C., if heat treatment is performed at a high temperature as described above, the Zn or Al partly melts. It is difficult to ensure, and there is a problem that Zn or Al is fused to the forming frame at the time of processing and adversely affects the forming.

また、上記のような高温成形は、強度を向上させる効果があるが、部品の側面では、微細組織が９０％以上のマルテンサイトで構成されて１０％未満の低い延伸率を有するため、耐衝突特性を十分に確保することが困難であり、適用できる自動車用部品に限界がある。   In addition, the high-temperature molding as described above has an effect of improving strength, but on the side of the component, the microstructure is composed of martensite of 90% or more and has a low stretch ratio of less than 10%, so that it is resistant to collision. It is difficult to ensure sufficient characteristics, and there are limits to the applicable automotive parts.

韓国特許出願公開公報第２００７−００５７６８９号Korean Patent Application Publication No. 2007-0057689 米国特許６,２９６,８０５号US Pat. No. 6,296,805

本発明の一側面は、温間プレス成形により、高い強度を有するとともに優れた延伸率を確保して、衝突特性に優れた温間プレス成形用鋼板及びこれを用いた温間プレス成形部材を提供する。   One aspect of the present invention provides a warm press-formed steel sheet having high strength and a high stretch ratio by using warm press forming and having excellent impact properties, and a warm press-formed member using the same. To do.

また、本発明の一側面は、めっきされた鋼板の場合、温間プレス成形のような熱処理によっても、優れた耐食性を確保することができる温間プレス成形用鋼板及び温間プレス成形部材を提供する。   In addition, in the case of a plated steel sheet, one aspect of the present invention provides a steel sheet for warm press forming and a warm press formed member that can ensure excellent corrosion resistance even by heat treatment such as warm press forming. To do.

本発明は、重量％で、Ｃ：０．０１〜０．５％、Ｓｉ：３．０％以下（０は除く）、Ｍｎ：３〜１５％、Ｐ：０．０００１〜０．１％、Ｓ：０．０００１〜０．０３％、Ａｌ：３．０％以下（０は除く）、Ｎ：０．０３％以下（０は除く）、Ｆｅ及び不可避な不純物を含む温間プレス成形用鋼板を提供する。   The present invention, by weight, C: 0.01-0.5%, Si: 3.0% or less (excluding 0), Mn: 3-15%, P: 0.0001-0.1%, S: 0.0001 to 0.03%, Al: 3.0% or less (excluding 0), N: 0.03% or less (excluding 0), steel for warm press forming containing Fe and inevitable impurities I will provide a.

また、本発明は、上記組成を有する鋼スラブを１０００〜１４００℃の温度において加熱する段階と、上記加熱された鋼スラブを熱間圧延し、Ａｒ３〜１０００℃の温度において仕上げ熱間圧延する段階と、上記熱間圧延後のＭｓ温度超過８００℃以下の温度において巻取して熱延鋼板を製造する段階とを含む温間プレス成形用鋼板の製造方法を提供する。   The present invention also includes a step of heating a steel slab having the above composition at a temperature of 1000 to 1400 ° C., and a step of hot rolling the heated steel slab and finishing hot rolling at a temperature of Ar 3 to 1000 ° C. And a step of producing a hot-rolled steel sheet by winding at a temperature of 800 ° C. or less exceeding the Ms temperature after the hot rolling.

また、本発明は、上記組成を有し、温間プレス成形及び冷却後の微細組織において、残留オーステナイトを体積分率で３〜５０％含み、残りはフェライト、マルテンサイト、焼戻マルテンサイト、及びベイナイトのうち１種以上である温間プレス成形部材を提供する。   Further, the present invention has the above composition, and in the fine structure after warm press forming and cooling, the retained austenite is contained in a volume fraction of 3 to 50%, and the remainder is ferrite, martensite, tempered martensite, and A warm press-formed member that is one or more of bainite is provided.

また、本発明は、上記組成を有する鋼板に温間プレス成形を行う段階と、上記温間プレス成形後に冷却する段階とを含み、上記温間プレス成形は１〜１０００℃／秒の昇温速度でＡｃ１〜Ａｃ３の温度範囲まで加熱し、上記加熱後に１〜１００００秒間温度を維持する熱処理を含む温間プレス成形部材の製造方法を提供する。   The present invention also includes a step of performing warm press forming on the steel sheet having the above composition, and a step of cooling after the warm press forming, wherein the warm press forming is performed at a heating rate of 1 to 1000 ° C./second. The manufacturing method of the warm press-molded member including the heat processing which heats to the temperature range of Ac1-Ac3, and maintains temperature for 1-10000 second after the said heating is provided.

本発明は、自動車構造部材及び補強材、特に衝突吸収が必要な部材に用いられることができる超高強度鋼板の製造方法及び温間プレス成形によって製造されたその部材に関するもので、温間プレス成形の熱処理による引張強度１０００ＭＰａ以上の超高強度及び延性に優れた鋼板の製造方法及びこれを用いた熱処理部材を提供することにより、熱処理型超高強度鋼を衝突部材まで拡大して適用することができる。   The present invention relates to a method for manufacturing an ultra-high strength steel sheet that can be used for automobile structural members and reinforcing materials, particularly members that need to absorb collisions, and the members manufactured by warm press forming. By providing a method for producing a steel sheet having an ultra high strength and ductility excellent in tensile strength of 1000 MPa or more by heat treatment and a heat treatment member using the same, the heat treatment type ultra high strength steel can be applied to a collision member. it can.

図１は、関連技術の熱間プレス成形に関する熱履歴を示すグラフである。FIG. 1 is a graph showing a thermal history related to hot press forming in the related art. 図２は、本発明の温間プレス成形に関する熱履歴を示すグラフである。FIG. 2 is a graph showing a thermal history relating to the warm press forming of the present invention.

本発明において、「温間プレス成形」とは、鋼板を一定の形態に加工することを意味する。つまり、上述のオーステナイト単相域を超える温度において熱処理して加工する熱間成形とは異なり、オーステナイト単相域以下の温度において熱処理して加工することを意味する。   In the present invention, “warm press forming” means that a steel plate is processed into a certain form. In other words, unlike hot forming in which heat treatment is performed at a temperature exceeding the above-described austenite single phase region, heat treatment is performed at a temperature below the austenite single phase region.

本発明において、上記温間プレス成形は熱処理及び成形を含み、これには熱処理後に成形する方式のみならず、成形後に熱処理する方式もすべて含まれる。   In the present invention, the warm press forming includes heat treatment and forming, and this includes not only a method of forming after heat treatment but also a method of performing heat treatment after forming.

本発明者らは、温間プレス成形によって部材（部品）を製造するにあたり、成分、微細組織、及び温間プレス成形時の熱処理温度を適切に制御する場合、部材の延伸率を向上させることができる点を見出し、本発明を完成させた。   In producing a member (part) by warm press molding, the present inventors can improve the stretch ratio of the member when appropriately controlling the components, the microstructure, and the heat treatment temperature during warm press molding. The present inventors have found a possible point and completed the present invention.

関連技術の熱間熱処理部材の製造方法では、部材においてマルテンサイトを主相として確保し、フェライトの生成を抑制するために、オーステナイト単相域を超える温度まで加熱した後、鋼板を成形し、Ｍｆ（マルテンサイト生成の終了）温度未満まで急冷させてマルテンサイトを主相にする高強度部材を製造する。   In the related-art hot-heat member manufacturing method of related art, in order to secure martensite as the main phase in the member and suppress the formation of ferrite, the steel sheet is formed after heating to a temperature exceeding the austenite single phase region, and Mf (End of martensite production) A high-strength member having martensite as the main phase is produced by rapid cooling to below the temperature.

しかし、本発明では、オーステナイト単相域以下の温度において熱処理及び成形して冷却する温間プレス成形法を用いることを特徴とする。オーステナイト単相域以下の温度において加熱及び維持するとき、粒界または粒内に生成されたオーステナイトにおいてＣ、Ｍｎなどが濃化されて形成されたオーステナイトを成形してから冷却すると、常温まで安定化させることができる点に着目した。   However, the present invention is characterized by using a warm press molding method in which heat treatment, molding, and cooling are performed at a temperature below the austenite single phase region. When heated and maintained at a temperature below the austenite single-phase region, when austenite formed by concentrating C, Mn, etc. in the austenite produced at the grain boundaries or in the grains is cooled after cooling, it stabilizes to room temperature. We focused on the points that can be made.

以下では、本発明の温間プレス成形用鋼板について詳細に説明する。   Below, the steel plate for warm press forming of this invention is demonstrated in detail.

（温間プレス成形鋼板）
まず、本発明の温間プレス成形鋼板の組成について詳細に説明する（以下、重量％）。 (Warm press-formed steel sheet)
First, the composition of the warm press-formed steel sheet of the present invention will be described in detail (hereinafter referred to as weight%).

炭素（Ｃ）：０．０１〜０．５％
上記Ｃは、鋼板の強度を増加させるための必須の元素であるのみならず、本発明において具現しようとする残留オーステナイトを確保するために、適正に添加する必要がある。Ｃ含有量が０．０１％未満の場合は、十分な強度を得ることができない上、温間プレス成形時に部材が３体積％以上の残留オーステナイトを確保することが困難である。よって、上記のような特徴を発揮するためには、０．０１％以上（好ましくは０．０５％以上）添加する。また、０．５％を超過して含有すると、熱延鋼板の冷間圧延性を低下させる上、高すぎる強度が得られ、所望する延伸率を確保することが困難であり、溶接性が低下しやすいことから、０．５％以下（好ましくは０．４％以下、より好ましくは０．３％以下）添加する。 Carbon (C): 0.01 to 0.5%
The C is not only an essential element for increasing the strength of the steel sheet, but also needs to be added appropriately in order to ensure retained austenite to be embodied in the present invention. If the C content is less than 0.01%, sufficient strength cannot be obtained, and it is difficult for the member to ensure 3% by volume or more of retained austenite during warm press molding. Therefore, in order to exhibit the above characteristics, 0.01% or more (preferably 0.05% or more) is added. On the other hand, if the content exceeds 0.5%, the cold-rollability of the hot-rolled steel sheet is deteriorated, and an excessively high strength is obtained. Therefore, 0.5% or less (preferably 0.4% or less, more preferably 0.3% or less) is added.

シリコン（Ｓｉ）：３．０％以下（０は除く）
上記Ｓｉは、製鋼において脱酸剤の役割を果たすのみならず、熱処理時に炭化物の生成を抑制する元素として添加する。Ｓｉ含有量が３％を超過すると、鋼板のめっき性を低下させるため、３％以下（好ましくは２．５％以下、より好ましくは２％以下）添加する。 Silicon (Si): 3.0% or less (excluding 0)
The Si is added not only as a deoxidizer in steelmaking, but also as an element that suppresses the formation of carbides during heat treatment. If the Si content exceeds 3%, the plateability of the steel sheet is lowered, so 3% or less (preferably 2.5% or less, more preferably 2% or less) is added.

アルミニウム（Ａｌ）：３．０％以下（０は除く）
上記Ａｌは、製鋼において脱酸作用をして鋼の清浄性を高める上、Ｓｉと同様に熱処理時に炭化物の生成を抑制する元素として添加する。Ａｌは、添加量の増加により、二相域が拡大して焼鈍温度の作業範囲が拡大されるという長所があるが、Ａｌ含有量が３％を超過すると、鋼板のめっき性が低下するのみならず、製造費用が上昇するため、上限を３％以下（好ましくは２．５％以下、より好ましくは２％以下）添加する。 Aluminum (Al): 3.0% or less (excluding 0)
The above-mentioned Al is added as an element that suppresses the formation of carbides during heat treatment, as well as Si, in addition to deoxidizing the steel to improve the cleanliness of the steel. Al has the advantage that the working range of the annealing temperature is expanded by increasing the addition amount, but the working range of the annealing temperature is expanded. However, if the Al content exceeds 3%, the plateability of the steel sheet only deteriorates. However, since the manufacturing cost increases, an upper limit of 3% or less (preferably 2.5% or less, more preferably 2% or less) is added.

マンガン（Ｍｎ）：３〜１５％
上記Ｍｎは、本発明において非常に重要な役割をする。Ｍｎは、固溶強化元素である上、Ｍｓ温度（マルテンサイトの変態開始温度）を下げる役割をしてオーステナイトの常温安定性を高める。また、Ｍｎは、Ａｃ１及びＡｃ３の温度を下げるため、本発明で求められる温間プレスの成形に重要な元素である。なお、Ａｃ１〜Ａｃ３の温度において温間プレスの成形及び熱処理時に生成されるオーステナイトにＭｎが拡散されてオーステナイトの常温安定性をさらに高めることができる。Ｍｎ含有量が３％未満の場合は、上記作用を十分に行うための強度が不足するため、３％以上（好ましくは４％以上、より好ましくは５％以上）添加する。また、１５％を超えると、製造費用が上昇する上、あまりにも多くの残留オーステナイトが生成されて、延伸率は十分に上昇させることができるものの、十分な強度を確保することは困難であるため、１５％以下（好ましくは１３％以下、より好ましくは１１％以下）添加する。 Manganese (Mn): 3-15%
The Mn plays a very important role in the present invention. Mn is a solid solution strengthening element and also serves to lower the Ms temperature (martensite transformation start temperature), thereby increasing the normal temperature stability of austenite. Further, Mn is an important element for forming the warm press required in the present invention in order to lower the temperatures of Ac1 and Ac3. In addition, Mn is diffused in the austenite produced at the time of Ac1-Ac3 at the time of shaping | molding of a warm press and heat processing, and the normal temperature stability of austenite can further be improved. When the Mn content is less than 3%, the strength for sufficiently performing the above action is insufficient, so 3% or more (preferably 4% or more, more preferably 5% or more) is added. On the other hand, if it exceeds 15%, the production cost will increase and too much retained austenite will be generated, and the draw ratio can be increased sufficiently, but it is difficult to ensure sufficient strength. 15% or less (preferably 13% or less, more preferably 11% or less).

リン（Ｐ）：０．０００１〜０．１％
上記Ｐは、Ｓｉと同様にマルテンサイトの熱処理時に炭化物の生成を抑制させる効果があるが、過剰に含有されると、溶接性が劣化し、粒界が弱くなるため、上限を０．１％に限定する。また、Ｐを０．０００１％未満に制御するためには、多くの製造費用がかかるため、その下限は０．０００１％に限定する。 Phosphorus (P): 0.0001 to 0.1%
P, like Si, has the effect of suppressing the formation of carbides during the heat treatment of martensite, but if contained excessively, the weldability deteriorates and the grain boundary becomes weak, so the upper limit is 0.1%. Limited to. Further, in order to control P to be less than 0.0001%, many manufacturing costs are required, so the lower limit is limited to 0.0001%.

硫黄（Ｓ）：０．０００１〜０．０３％
上記Ｓは、鋼中に不純物として存在し、鋼板の延性及び溶接性を阻害する元素である。Ｓ含量が０．０３％以下の場合は、このような悪影響が大きくないため、その上限を０．０３％にする。また、Ｓを０．０００１％未満に制御するためには、多くの製造費用がかかるため、その下限を０．０００１％に限定する。 Sulfur (S): 0.0001 to 0.03%
Said S exists as an impurity in steel, and is an element which inhibits the ductility and weldability of a steel plate. When the S content is 0.03% or less, such an adverse effect is not great, so the upper limit is made 0.03%. Further, in order to control S to be less than 0.0001%, many manufacturing costs are required, so the lower limit is limited to 0.0001%.

窒素（Ｎ）：０．０３％以下（０は除く）
上記Ｎは、鋼中に不純物として含まれる。鋼板においてＮは、窒化物を形成させて水素による耐遅れ破壊特性を向上させるために添加される。Ｎ含量が０．０３を超過すると、連鋳時にスラブクラックに対する鋭敏性が増加し、スラブ内に気孔が発生しやすいため、その上限を０．０３％（好ましくは０．０２％以下、より好ましくは０．０１％以下）にする。 Nitrogen (N): 0.03% or less (excluding 0)
N is contained as an impurity in the steel. In the steel sheet, N is added to form nitrides and improve delayed fracture resistance due to hydrogen. When the N content exceeds 0.03, the sensitivity to slab cracks increases during continuous casting, and pores are likely to be generated in the slab, so the upper limit is 0.03% (preferably 0.02% or less, more preferably Is 0.01% or less).

本発明では、上記組成の他に、硬化能向上元素であるＣｒ、Ｍｏ、及びＷのうち１種以上、析出強化元素であるＴｉ、Ｎｂ、Ｚｒ、及びＶのうち１種以上、強度向上元素であるＣｕ及びＮｉのうち１種以上、粒界強化及び硬化能元素としてＢ、めっき性向上のためのＳｂ及びＳｎのうち１種以上をさらに添加することができる。   In the present invention, in addition to the above composition, one or more of Cr, Mo, and W that are hardening ability improving elements, one or more of Ti, Nb, Zr, and V that are precipitation strengthening elements, and a strength improving element. One or more of Cu and Ni, and B as grain boundary strengthening and hardening ability elements, and one or more of Sb and Sn for improving plating properties can be further added.

Ｃｒ、Ｍｏ、及びＷのうち１種以上の組み合わせ：０．００１〜２．０％
上記Ｃｒ、Ｍｏ、及びＷは、硬化能及び析出強化効果があり、高強度をさらに確保することができる。Ｃｒ、Ｍｏ、またはＷの含量が０．００１％未満の場合は、硬化能及び析出強化の効果を十分に得ることができず、２．０％を超過すると、その効果が飽和する上、製造費用が上昇するため、その上限を２．０％に制限する。 Combination of one or more of Cr, Mo, and W: 0.001 to 2.0%
The Cr, Mo, and W have a hardening ability and a precipitation strengthening effect, and can further ensure high strength. When the content of Cr, Mo, or W is less than 0.001%, the effects of hardening ability and precipitation strengthening cannot be obtained sufficiently. Since the cost increases, the upper limit is limited to 2.0%.

Ｔｉ、Ｎｂ、Ｚｒ、及びＶのうち１種以上の組み合わせ：０．００１〜０．４％
上記Ｔｉ、Ｎｂ、Ｚｒ、及びＶは、鋼板の強度上昇、結晶粒微細化及び熱処理特性を向上させる元素である。上記Ｔｉ、Ｎｂ、Ｚｒ、及びＶの含量が０．００１％未満の場合は、上記のような効果を期待することが困難であり、その含量が０．４％を超過すると、製造費用が過度に上昇する。よって、その含量を０．００１〜０．４％に制限することが好ましい。 A combination of one or more of Ti, Nb, Zr, and V: 0.001 to 0.4%
Ti, Nb, Zr, and V are elements that increase the strength of the steel sheet, refine crystal grains, and improve heat treatment characteristics. When the content of Ti, Nb, Zr, and V is less than 0.001%, it is difficult to expect the above effect. When the content exceeds 0.4%, the manufacturing cost is excessive. To rise. Therefore, it is preferable to limit the content to 0.001 to 0.4%.

Ｃｕ及びＮｉのうち１種以上の組み合わせ：０．００５〜２．０％
上記Ｃｕは、微細なＣｕ析出物を生成して強度を向上させる元素である。上記Ｃｕ含量が０．００５％未満の場合、所望する強度を十分に得ることができず、２．０％を超過すると、操業性を劣化させる可能性がある。よって、その含量を０．００５〜２．０％に制限することが好ましい。また、上記Ｎｉは、強度上昇及び熱処理性を向上させるのに有効な元素である。しかし、０．００５％未満の場合は、その効果を得ることができず、２．０％を超過すると、製造費用が上昇するため、その含量を０．００５〜２．０％に限定する。 One or more combinations of Cu and Ni: 0.005 to 2.0%
Cu is an element that generates fine Cu precipitates and improves strength. If the Cu content is less than 0.005%, the desired strength cannot be obtained sufficiently, and if it exceeds 2.0%, the operability may be deteriorated. Therefore, it is preferable to limit the content to 0.005 to 2.0%. Ni is an element effective for increasing the strength and improving the heat treatment property. However, if it is less than 0.005%, the effect cannot be obtained, and if it exceeds 2.0%, the manufacturing cost increases, so the content is limited to 0.005 to 2.0%.

Ｂ：０．０００１〜０．０１％
上記Ｂは、硬化能が大きい元素で、微量添加しても熱処理鋼において高い強度を確保することができる。また、結晶粒界を強化させて本発明の高Ｍｎ鋼における粒界脆性を抑制することができる。しかし、０．０００１％未満の場合は、このような効果を得ることができず、０．０１％を超過すると、その効果が飽和する上、熱間加工性の劣化をもたらすため、その上限を０．０１％に制限することが好ましい。 B: 0.0001 to 0.01%
B is an element having a high hardening ability, and even when added in a small amount, high strength can be secured in the heat-treated steel. Further, the grain boundary embrittlement in the high Mn steel of the present invention can be suppressed by strengthening the crystal grain boundary. However, when the content is less than 0.0001%, such an effect cannot be obtained. When the content exceeds 0.01%, the effect is saturated and the hot workability is deteriorated. It is preferable to limit to 0.01%.

Ｓｂ及びＳｎのうち１種以上の組み合わせ：０．０００１〜１．０％
上記Ｓｂ及びＳｎは、表面及び粒界濃化元素で、本発明において添加される多くのＭｎが焼鈍時に表面濃化されることにより、酸化物の生成によるめっき性の劣化を抑制することができる。しかし、０．０００１％未満の場合は、このような効果を得ることができず、１．０％を超過すると、熱間加工性が劣化するため、その上限を１．０％に制限することが好ましい。 One or more combinations of Sb and Sn: 0.0001 to 1.0%
The above Sb and Sn are surface and grain boundary concentrating elements, and a large amount of Mn added in the present invention is concentrated on the surface during annealing, so that it is possible to suppress deterioration of plating properties due to the formation of oxides. . However, if it is less than 0.0001%, such an effect cannot be obtained. If it exceeds 1.0%, the hot workability deteriorates, so the upper limit should be limited to 1.0%. Is preferred.

残りは、Ｆｅ及び不可避な不純物を含む。しかし、上記組成以外に含まれる他の組成は排除しない。   The remainder contains Fe and inevitable impurities. However, other compositions included in addition to the above composition are not excluded.

本発明の温間プレス成形用鋼板は、熱延鋼板、冷延鋼板及びめっき鋼板のうちいずれか一つであることが好ましく、その種類は特に限定しない。上記めっき鋼板は、Ｚｎ系めっき鋼板またはＡｌ系めっき鋼板であることが好ましい。   The warm press-formed steel plate of the present invention is preferably any one of a hot-rolled steel plate, a cold-rolled steel plate and a plated steel plate, and the type thereof is not particularly limited. The plated steel sheet is preferably a Zn-based plated steel sheet or an Al-based plated steel sheet.

上記温間プレス成形用鋼板の微細組織の主相は、マルテンサイト、ベイナイトまたはこれらの組み合わせが３０体積％以上であることが好ましい。上記マルテンサイト、ベイナイトまたはこれらの組み合わせが３０体積％未満の場合は、温間プレス成形の熱処理時にオーステナイトを十分に確保することが困難である上、求められる強度を十分に確保することも困難である。   As for the main phase of the microstructure of the steel sheet for warm press forming, martensite, bainite or a combination thereof is preferably 30% by volume or more. When the martensite, bainite, or a combination thereof is less than 30% by volume, it is difficult to sufficiently secure austenite during the heat treatment of warm press molding, and it is also difficult to sufficiently secure the required strength. is there.

以下では、本発明の温間プレス成形用鋼板の製造方法について詳細に説明する。   Below, the manufacturing method of the steel plate for warm press forming of this invention is demonstrated in detail.

（温間プレス成形用鋼板の製造方法）
上記組成を有する鋼スラブを１０００〜１４００℃において加熱した後、熱間圧延を行う。上記加熱温度が１０００℃の未満では、連鋳組織の均質化が十分に確保されず、１４００℃を超過すると製造費用が上昇する。 (Method for producing warm press-formed steel sheet)
A steel slab having the above composition is heated at 1000 to 1400 ° C. and then hot-rolled. If the heating temperature is less than 1000 ° C., homogenization of the continuous cast structure is not sufficiently ensured, and if it exceeds 1400 ° C., the manufacturing cost increases.

その後、Ａｒ３温度以上１０００℃以下の温度において熱間仕上げ圧延を行う。上記熱間仕上げ圧延温度がＡｒ３温度未満の場合、二相域圧延になって熱延混粒を発生させ、操業性を劣化させる。また、１０００℃を超過すると、結晶粒粗大化をもたらし、多くの酸化スケールを生成させる。   Thereafter, hot finish rolling is performed at a temperature not lower than Ar3 and not higher than 1000 ° C. When the said hot finish rolling temperature is less than Ar3 temperature, it becomes a two-phase area rolling, a hot-rolled mixed grain is generated, and operativity is deteriorated. On the other hand, when the temperature exceeds 1000 ° C., it causes coarsening of crystal grains and generates a lot of oxide scale.

次に、Ｍｓ温度超過８００℃以下の温度において巻取する。Ｍｓ温度の以下の温度では、熱延巻取機に負荷を与える可能性があり、８００℃を超過すると、熱延鋼板の酸化層の厚さが増加するという短所がある。   Next, it winds in the temperature below Ms temperature and 800 degrees C or less. At a temperature below the Ms temperature, there is a possibility that a load is applied to the hot-rolling winder. When the temperature exceeds 800 ° C., the thickness of the oxide layer of the hot-rolled steel sheet increases.

このようにして製造された熱延鋼板は温間プレス成形に直接用いたり、酸洗をさらに行ってから用いたりすることができる。また、上記酸洗された鋼板にＺｎ系めっきまたはＡｌ系めっきを施しためっき鋼板を温間プレス成形に用いることもできる。   The hot-rolled steel sheet thus produced can be used directly for warm press forming or after further pickling. Further, a plated steel sheet obtained by performing Zn-based plating or Al-based plating on the pickled steel sheet can also be used for warm press forming.

上記熱延鋼板に酸洗及び冷間圧延を行うことにより、冷延鋼板を製造することができる。上記酸洗は一般の方法によって行われ、上記冷間圧延時の冷間圧下率は本発明では限定されず、一般の冷延鋼板の製造方法による。   A cold-rolled steel sheet can be produced by pickling and cold-rolling the hot-rolled steel sheet. The pickling is performed by a general method, and the cold rolling reduction during the cold rolling is not limited in the present invention, and depends on a general method for manufacturing a cold-rolled steel sheet.

好ましい一例として、上記冷延鋼板を製造するにあたり、冷間圧延前に箱焼鈍を行うことができる。上記箱焼鈍は、上記のように製造された熱延鋼板の強度を高めることができる。これは、冷間圧延の負荷を大きくするため、箱焼鈍によって熱延鋼板の強度を減らし、冷間圧延性を向上させるためである。上記箱焼鈍において、熱処理温度はＡｃ１〜Ａｃ３の温度範囲で行われることが好ましい。上記Ａｃ１温度未満の場合、熱延鋼板の強度下落を十分に確保することができず、Ａｃ３温度を超過すると、製造費用が上昇し、再び徐冷したときに多量のマルテンサイトが生成されて熱延鋼板の強度が十分に低減しない。よって、上記箱焼鈍を行った後に、冷間圧延を行うことで冷延鋼板を製造することができる。   As a preferred example, in producing the cold-rolled steel sheet, box annealing can be performed before cold rolling. The box annealing can increase the strength of the hot-rolled steel sheet manufactured as described above. This is to reduce the strength of the hot-rolled steel sheet by box annealing and increase the cold rolling property in order to increase the cold rolling load. In the box annealing, the heat treatment temperature is preferably performed in a temperature range of Ac1 to Ac3. If the temperature is lower than the Ac1 temperature, the strength of the hot-rolled steel sheet cannot be sufficiently lowered. If the temperature exceeds the Ac3 temperature, the manufacturing cost increases, and a large amount of martensite is generated when the steel is slowly cooled again. The strength of the rolled steel sheet is not reduced sufficiently. Therefore, a cold-rolled steel sheet can be manufactured by performing cold rolling after performing the box annealing.

上記冷延鋼板を連続焼鈍熱処理して焼鈍鋼板を製造することができる。上記連続焼鈍熱処理条件は、特に限定されないが、７００〜９００℃において行うことが好ましい。焼鈍温度が７００℃未満の場合は、鋼板の再結晶を十分に確保することができず、９００℃を超過すると、製造費用が上昇する上、操業にも困難をきたす。また、上記焼鈍鋼板にＺｎ−Ｎｉ電気めっきを行うことにより、Ｚｎ−Ｎｉ電気めっき鋼板を製造することができる。   The cold-rolled steel sheet can be subjected to continuous annealing heat treatment to produce an annealed steel sheet. Although the said continuous annealing heat processing conditions are not specifically limited, It is preferable to carry out at 700-900 degreeC. When the annealing temperature is less than 700 ° C, sufficient recrystallization of the steel sheet cannot be ensured, and when it exceeds 900 ° C, the manufacturing cost increases and operation becomes difficult. Moreover, a Zn-Ni electroplated steel sheet can be manufactured by performing Zn-Ni electroplating on the annealed steel sheet.

また、上記冷延鋼板にＺｎ系めっきまたはＡｌ系めっきを行い、鋼板の耐食性及び耐熱性を確保する。Ｚｎめっき鋼板の熱処理及びめっき条件は、特に限定されないが、一般の溶融亜鉛めっき鋼板（ＧＩ）または合金化溶融亜鉛めっき鋼板（ＧＡ）が製造されることが好ましい。なお、Ａｌめっき鋼板の熱処理及びめっき条件も、特に限定されず、一般の製造工程によって行われる。   In addition, Zn-based plating or Al-based plating is performed on the cold-rolled steel sheet to ensure the corrosion resistance and heat resistance of the steel sheet. The heat treatment and plating conditions of the Zn-plated steel sheet are not particularly limited, but it is preferable that a general hot-dip galvanized steel sheet (GI) or an alloyed hot-dip galvanized steel sheet (GA) is produced. In addition, the heat treatment and plating conditions of the Al-plated steel sheet are not particularly limited, and are performed by a general manufacturing process.

以下では、上記のように製造された鋼板による温間プレス成形を用いて製造された本発明の温間プレス成形部材について詳細に説明する。   Below, the warm press molding member of this invention manufactured using the warm press molding by the steel plate manufactured as mentioned above is demonstrated in detail.

（温間プレス成形部材）
本発明の温間プレス成形部材は、上記温間プレス成形鋼板の組成を有し、微細組織の残留オーステナイトを体積分率で３〜５０％含み、残りはフェライト、マルテンサイト、焼戻マルテンサイト、及びベイナイトのうち１種以上を含むことが好ましい。 (Warm press-formed material)
The warm press-formed member of the present invention has the composition of the above-mentioned warm press-formed steel sheet, contains 3 to 50% of the retained austenite of the microstructure in volume fraction, the rest is ferrite, martensite, tempered martensite, And it is preferable that 1 or more types are included among bainite.

上記残留オーステナイト分率が体積％で、３％未満の場合は、本発明において目標とする超高強度及び高延伸率を確保することが困難であり、５０％を超過すると、鋼板に多くのＣやＭｎなどを添加しなければならないため製造が困難である。残留オーステナイトの他に、残りの組織として、フェライト、マルテンサイト、焼戻マルテンサイト、ベイナイトなどを含有することができる。   When the residual austenite fraction is less than 3% by volume, it is difficult to ensure the ultra-high strength and high stretch ratio that are the targets in the present invention. Since Mn and Mn must be added, production is difficult. In addition to the retained austenite, ferrite, martensite, tempered martensite, bainite and the like can be contained as the remaining structure.

上記フェライトは、後述する温間プレス成形過程の熱処理時に生成されたり、熱処理前に一部含まれ得る。このようなフェライトの分率は、３０％以下であることが好ましい。フェライト分率が３０％を超過すると、所望する強度を十分に確保することが困難である。   The ferrite may be generated during the heat treatment in the warm press forming process described later, or may be partially included before the heat treatment. The ferrite fraction is preferably 30% or less. If the ferrite fraction exceeds 30%, it is difficult to sufficiently secure the desired strength.

上記マルテンサイトも、温間プレス成形過程の熱処理前に生成されたり、熱処理後に生成され得る。このとき、マルテンサイト内には一部炭化物が生成される可能性がある。このようなマルテンサイトは５０〜９５％であることが好ましい。マルテンサイト分率が５０％未満の場合は、所望する強度を十分に確保することが困難であり、９５％を超過すると、残留オーステナイトを十分に確保することが困難である。   The martensite can also be generated before or after the heat treatment in the warm press forming process. At this time, a part of carbide may be generated in the martensite. Such martensite is preferably 50 to 95%. When the martensite fraction is less than 50%, it is difficult to sufficiently secure the desired strength, and when it exceeds 95%, it is difficult to sufficiently secure retained austenite.

以下では、上記温間プレス成形部材の製造方法について詳細に説明する。   Below, the manufacturing method of the said warm press molding member is demonstrated in detail.

（温間プレス成形部材の製造方法）
延伸率に優れた部材を製造するために、本発明では温間プレス成形方法を採用する。本発明者らは、Ａｃ３温度の以下における熱処理時にめっき層の耐熱性を確保することができる点に着目し、温間プレス成形を用いて所望する材質を十分に確保することができる方法を研究した。その結果、上記のような鋼成分を有する鋼板を用いることにより、Ａｃ３温度以下において熱処理して残留オーステナイトを確保することができる点を見出した。 (Method for producing warm press-formed member)
In order to produce a member having an excellent stretch rate, a warm press molding method is employed in the present invention. The inventors focused on the fact that the heat resistance of the plating layer can be secured during heat treatment at a temperature below the Ac3 temperature, and researched a method that can sufficiently secure the desired material using warm press molding. did. As a result, it has been found that by using a steel plate having the steel components as described above, it is possible to ensure retained austenite by heat treatment at an Ac3 temperature or lower.

即ち、Ｍｎが添加された鋼が適正な熱間圧延及び／または冷間圧延、焼鈍を経ると、熱処理前の微細組織から５μｍ以下の非常に微細な組織を得るのに有用であることを見出した。また、熱処理前の微細組織がマルテンサイト及び／またはベイナイトを十分に確保すると、マルテンサイト及び／またはベイナイトのナノサイズのラス（Ｌａｔｈ）粒界または結晶粒界において、Ｍｎ及びＣが温間プレス成形のための熱処理時にオーステナイトに濃化されて、多量のオーステナイトが常温まで安定化されることを究明した。このとき、上述したように、温間プレス成形用鋼板の微細組織の主相は、マルテンサイト、ベイナイト、またはこれらの組み合わせが３０％以上であることが好ましい。これは、その分率が少ないと、温間プレス成形の熱処理時にオーステナイトを十分に確保することが困難である上、求められる強度を確保することが困難であるためである。   That is, it has been found that when steel added with Mn is subjected to appropriate hot rolling and / or cold rolling and annealing, it is useful to obtain a very fine structure of 5 μm or less from the fine structure before heat treatment. It was. In addition, when the microstructure before heat treatment sufficiently secures martensite and / or bainite, Mn and C are warm-pressed at the marsitic and / or bainite nano-sized lath grain boundaries or crystal grain boundaries. It has been found that a large amount of austenite is stabilized to room temperature by being concentrated to austenite during the heat treatment. At this time, as described above, the main phase of the microstructure of the steel sheet for warm press forming is preferably 30% or more of martensite, bainite, or a combination thereof. This is because if the fraction is small, it is difficult to sufficiently secure austenite at the time of heat treatment in warm press molding and it is difficult to ensure the required strength.

このような原理を用いて製造された部材では、残留オーステナイトが体積％で３％以上含有されて優れた延伸率を有する。   In a member manufactured using such a principle, the retained austenite is contained in an amount of 3% or more by volume and has an excellent stretch ratio.

本発明の温間プレス成形部材の製造方法は、まず、上記のように製造された鋼板に温間プレス成形を行う。上記温間プレス成形は、熱処理後に成形する方法、及び成形後に熱処理する方法のいずれでもよい。   In the method for manufacturing a warm press-formed member of the present invention, first, warm press forming is performed on the steel plate manufactured as described above. The warm press forming may be either a method of forming after heat treatment or a method of performing heat treatment after forming.

温間プレス成形の熱処理条件について説明すると、１〜１０００℃／秒の昇温速度で加熱し、温度範囲はＡｃ１〜Ａｃ３の温度範囲で加熱する。上記加熱後に１〜１００００秒間その温度を維持する。   The heat treatment conditions for warm press forming will be described. Heating is performed at a temperature rising rate of 1 to 1000 ° C./second, and the temperature range is heated within the temperature range of Ac1 to Ac3. The temperature is maintained for 1 to 10,000 seconds after the heating.

上記昇温速度が１℃／秒の未満の場合は、製造費用が上昇し、生産性が低下しやすいため、その下限を１℃／秒にすることが好ましく、昇温速度１０００℃／秒を超過すると、過度な加熱設備が求められる上、本発明の作用効果があまり大きくないため、その上限を１０００℃／秒にすることが好ましい。   When the temperature rising rate is less than 1 ° C./second, the manufacturing cost increases, and the productivity tends to decrease. Therefore, the lower limit is preferably 1 ° C./second, and the temperature rising rate is 1000 ° C./second. If it exceeds, an excessive heating facility is required, and the effect of the present invention is not so great, so the upper limit is preferably set to 1000 ° C./second.

上記Ａｃ１〜Ａｃ３の温度範囲は、残留オーステナイトを確保するのに重要な役割をする。上記温度がＡｃ１未満の場合は、熱処理前のマルテンサイトまたはベイナイトの粒界または粒内にオーステナイトが生成されない可能性があるため、本発明において求められる残留オーステナイトを確保することができない。したがって、熱処理はＡｃ１以上の温度（好ましくはＡｃ１＋１０℃以上、より好ましくはＡｃ１＋２０℃以上）で実施される。また、Ａｃ３を超過すると、Ｃ及びＭｎがオーステナイトに十分に濃化されないため、残留オーステナイトの安定性が低下し、所望する残留オーステナイトを十分に確保することが困難になり、その結果、強度は上昇するが、延伸率を十分に確保することは困難であるため、その上限をＡｃ３（好ましくはＡｃ３−１０℃以下、より好ましくはＡｃ３−２０℃以下）とする。   The temperature range of Ac1 to Ac3 plays an important role in securing retained austenite. When the temperature is less than Ac1, austenite may not be generated in the grain boundaries or grains of martensite or bainite before the heat treatment, and thus the retained austenite required in the present invention cannot be ensured. Therefore, the heat treatment is performed at a temperature of Ac1 or higher (preferably Ac1 + 10 ° C. or higher, more preferably Ac1 + 20 ° C. or higher). In addition, if Ac3 is exceeded, C and Mn are not sufficiently concentrated in austenite, so the stability of retained austenite is lowered and it is difficult to sufficiently secure the desired retained austenite, resulting in an increase in strength. However, since it is difficult to ensure a sufficient stretching ratio, the upper limit is set to Ac3 (preferably Ac3-10 ° C. or lower, more preferably Ac3-20 ° C. or lower).

上記維持時間が１００００秒を超過すると、生産性が低下する上、熱処理前のマルテンサイトが分解されて強度を十分に確保することが困難であるため、その上限を１００００秒とする。   When the maintenance time exceeds 10,000 seconds, productivity is lowered and martensite before heat treatment is decomposed and it is difficult to sufficiently secure the strength. Therefore, the upper limit is set to 10,000 seconds.

その後、温間プレス成形を行ってから冷却する。このとき、冷却速度の範囲は、特に限定されないが、好ましくは１〜１０００℃／秒の冷却速度で行うことが好ましい。冷却速度が１℃／秒未満の場合は、部材の生産性を十分に確保することが困難である上、冷却速度を制御するための設備がさらに必要になるため製造費用が上昇する。また、冷却速度が１０００℃／秒を超過すると、急冷を十分に行うための設備が必要になる上、上記温間プレス成形部材の組織確保に役立たない。   Then, it cools after performing warm press molding. At this time, the range of the cooling rate is not particularly limited, but the cooling rate is preferably 1 to 1000 ° C./sec. When the cooling rate is less than 1 ° C./second, it is difficult to sufficiently secure the productivity of the member, and more equipment for controlling the cooling rate is required, resulting in an increase in manufacturing cost. On the other hand, if the cooling rate exceeds 1000 ° C./second, equipment for sufficiently performing rapid cooling is required, and it is not useful for securing the structure of the warm press-formed member.

以下では、本発明の実施例について詳細に説明する。下記実施例は、本発明の理解を助けるためのものに過ぎず、本発明を限定するものではない。   Below, the Example of this invention is described in detail. The following examples are only for helping understanding of the present invention, and do not limit the present invention.

下記表１の組成を有する鋼スラブを真空溶解し、加熱炉で再加熱温度１２００℃において１時間加熱し、熱間圧延を行った。このとき、熱間圧延は９００℃において終了し、炉冷温度を６８０℃にして熱延鋼板を製造した。このようにして製造された熱延鋼板に対して温間プレス成形のシミュレーションを行った。   A steel slab having the composition shown in Table 1 below was melted in vacuum and heated in a heating furnace at a reheating temperature of 1200 ° C. for 1 hour to perform hot rolling. At this time, the hot rolling was finished at 900 ° C., and the furnace cooling temperature was set to 680 ° C. to produce a hot rolled steel sheet. A simulation of warm press forming was performed on the hot-rolled steel sheet thus manufactured.

また、上記熱延鋼板を用いて酸洗を行った後、酸洗された熱延鋼板を用意し、冷間圧下率５０％で冷延鋼板を製造した。特に、鋼種Ｍ及びＮは、冷間圧延後に箱焼鈍熱処理を行った。上記箱焼鈍熱処理条件は、３０℃／ｈで昇温し、６００℃において１０時間維持した後、３０℃／ｈの冷却速度で冷却した。一方、上記箱焼鈍処理しない場合は、７８０℃の温度で連続焼鈍を行った。   Moreover, after pickling using the said hot-rolled steel plate, the pickled hot-rolled steel plate was prepared and the cold-rolled steel plate was manufactured with the cold reduction rate of 50%. In particular, steel types M and N were subjected to box annealing heat treatment after cold rolling. The box annealing heat treatment conditions were as follows: the temperature was raised at 30 ° C./h, maintained at 600 ° C. for 10 hours, and then cooled at a cooling rate of 30 ° C./h. On the other hand, when the box annealing treatment was not performed, continuous annealing was performed at a temperature of 780 ° C.

なお、上記酸洗された熱延鋼板及び冷延鋼板にＺｎめっきまたはＡｌめっきを行い、めっき鋼板をともに製造した。上記ＺｎめっきまたはＡｌめっきは、焼鈍温度７８０℃において熱処理した後、それぞれＺｎめっき浴及びＡｌめっき浴に浸漬して行われた。   The pickled hot-rolled steel sheet and cold-rolled steel sheet were subjected to Zn plating or Al plating to produce both plated steel sheets. The Zn plating or Al plating was performed by heat treatment at an annealing temperature of 780 ° C., and then immersed in a Zn plating bath and an Al plating bath, respectively.

このようにして製造及び酸洗された熱延鋼板、冷延鋼板及びめっき鋼板を用いて温間プレス成形工程の熱処理条件でシミュレーションを行った。熱処理条件は、表２に示した通りである。このとき、昇温速度は３℃／秒にした。   The simulation was performed under the heat treatment conditions of the warm press forming process using the hot rolled steel sheet, cold rolled steel sheet and plated steel sheet thus manufactured and pickled. The heat treatment conditions are as shown in Table 2. At this time, the temperature rising rate was 3 ° C./second.

上記のように温間プレス成形工程がシミュレーションされた鋼板の機械的性質及び残留オーステナイト分率をＪＩＳ Ｚ ２２０１ ５号の引張試験片を用いて測定した。上記残留オーステナイト分率は、Ｘ線回折試験から得られたオーステナイト（２００）、（２２０）、（３１１）のピーク面積及びフェライト（２００）、（２１１）のピーク面積を求めて、下記式１のように５ピーク法で計算した。下記式１において、Ｖγはオーステナイト分率、Ｉαはフェライトのピーク面積、Ｉγはオーステナイトピークの面積を示す。 The mechanical properties and the retained austenite fraction of the steel sheet in which the warm press forming process was simulated as described above were measured using a tensile test piece of JIS Z 2201-5. The residual austenite fraction was obtained by calculating the peak areas of austenite (200), (220), (311) and the ferrite (200), (211) obtained from the X-ray diffraction test, and the following formula 1 Thus, the calculation was performed by the 5-peak method. In formula 1, V gamma austenite fraction, the I alpha peak area of the ferrite, the I gamma shows the area of the austenite peak.

Figure 2015503023
Figure 2015503023

これによって得られた最終鋼板の機械的性質及び残留オーステナイト分率を表２に示した。   Table 2 shows the mechanical properties and the retained austenite fraction of the final steel sheet thus obtained.

Figure 2015503023
Figure 2015503023

Figure 2015503023
Figure 2015503023

上記発明組成に該当する鋼種Ａ〜Ｐの場合は、最終製品における残留オーステナイト分率が３％以上と優れた延伸率を示すのに対し、比較鋼Ｑ及びＲの場合は、いかなる熱処理温度下においても残留オーステナイト分率が３％未満と劣化した延伸率を示すことが分かる。   In the case of steel types A to P corresponding to the above invention composition, the retained austenite fraction in the final product shows an excellent draw ratio of 3% or more, whereas in the case of comparative steels Q and R, under any heat treatment temperature It can also be seen that the residual austenite fraction shows a deteriorated stretch ratio of less than 3%.

また、Ａ鋼種において温間プレス成形時の熱処理温度をＡｃ３以上である８５０℃にした場合、強度は高くなるが、残留オーステナイトを十分に確保できないため延伸率が低下することが確認できた。   Moreover, when the heat treatment temperature at the time of warm press forming was 850 ° C. which is Ac3 or higher in the steel A type, the strength was increased, but the retained austenite could not be sufficiently secured, so that it was confirmed that the drawing ratio was lowered.

Claims (16)

重量％で、Ｃ：０．０１〜０．５％、Ｓｉ：３．０％以下（０は除く）、Ｍｎ：３〜１５％、Ｐ：０．０００１〜０．１％、Ｓ：０．０００１〜０．０３％、Ａｌ：３．０％以下（０は除く）、Ｎ：０．０３％以下（０は除く）、Ｆｅ及び不可避な不純物を含む、温間プレス成形用鋼板。   C: 0.01 to 0.5%, Si: 3.0% or less (excluding 0), Mn: 3 to 15%, P: 0.0001 to 0.1%, S: 0.005% by weight. A steel plate for warm press forming containing 0001 to 0.03%, Al: 3.0% or less (excluding 0), N: 0.03% or less (excluding 0), Fe and inevitable impurities. 前記鋼板は、Ｃｒ、Ｍｏ及びＷからなる群より選択された１種以上を０．００１〜２．０％さらに含む、請求項１に記載の温間プレス成形用鋼板。   The steel plate for warm press forming according to claim 1, wherein the steel plate further contains 0.001 to 2.0% of one or more selected from the group consisting of Cr, Mo and W. 前記鋼板はＴｉ、Ｎｂ、Ｚｒ及びＶからなる群より選択された１種以上を０．００１〜０．４％さらに含む、請求項１に記載の温間プレス成形用鋼板。   The steel plate for warm press forming according to claim 1, further comprising 0.001 to 0.4% of one or more selected from the group consisting of Ti, Nb, Zr and V. 前記鋼板は、ＣｕまたはＮｉの１種以上を０．００５〜２．０％さらに含む、請求項１に記載の温間プレス成形用鋼板。   The steel plate for warm press forming according to claim 1, wherein the steel plate further contains 0.005 to 2.0% of one or more kinds of Cu or Ni. 前記鋼板は、ＳｂまたはＳｎの１種以上を０．０００１〜１．０％さらに含む、請求項１に記載の温間プレス成形用鋼板。   The steel plate for warm press forming according to claim 1, wherein the steel plate further contains 0.0001 to 1.0% of one or more kinds of Sb or Sn. 前記鋼板は、Ｂ：０．０００１〜０．０１％をさらに含む、請求項１に記載の温間プレス成形用鋼板。   The steel plate for warm press forming according to claim 1, wherein the steel plate further includes B: 0.0001 to 0.01%. 前記鋼板は、熱延鋼板、冷延鋼板、Ｚｎ系めっき鋼板、及びＡｌ系めっき鋼板のうちいずれか一つである、請求項１に記載の温間プレス成形用鋼板。   The steel plate for warm press forming according to claim 1, wherein the steel plate is one of a hot-rolled steel plate, a cold-rolled steel plate, a Zn-based plated steel plate, and an Al-based plated steel plate. 前記鋼板の微細組織は、マルテンサイト、ベイナイト、またはこれらの組み合わせが３０体積％以上である、請求項１に記載の温間プレス成形用鋼板。   The steel sheet for warm press forming according to claim 1, wherein the microstructure of the steel sheet is 30% by volume or more of martensite, bainite, or a combination thereof. 重量％で、Ｃ：０．０１〜０．５％、Ｓｉ：３．０％以下（０は除く）、Ｍｎ：３〜１５％、Ｐ：０．０００１〜０．１％、Ｓ：０．０００１〜０．０３％、Ａｌ：３．０％以下（０は除く）、Ｎ：０．０３％以下（０は除く）、Ｆｅ及び不可避な不純物を含む鋼スラブを１０００〜１４００℃の温度において加熱する段階と、
前記加熱された鋼スラブを熱間圧延し、Ａｒ３〜１０００℃の温度において仕上げ熱間圧延する段階と、
前記熱間圧延後にＭｓ温度超過８００℃以下において巻取して熱延鋼板を製造する段階
とを含む、温間プレス成形用鋼板の製造方法。 C: 0.01 to 0.5%, Si: 3.0% or less (excluding 0), Mn: 3 to 15%, P: 0.0001 to 0.1%, S: 0.005% by weight. Steel slab containing 0001 to 0.03%, Al: 3.0% or less (excluding 0), N: 0.03% or less (excluding 0), Fe and inevitable impurities at a temperature of 1000 to 1400 ° C. Heating, and
Hot rolling the heated steel slab and finishing hot rolling at a temperature of Ar3-1000 ° C;
A method of manufacturing a hot-pressed steel sheet, comprising: a step of winding a hot-rolled steel sheet at a temperature exceeding 800 ° C. after the hot rolling to produce a hot-rolled steel sheet. 前記熱延鋼板を箱焼鈍する段階と、
前記箱焼鈍後に冷間圧延して冷延鋼板を製造する段階
とを含む、請求項９に記載の温間プレス成形用鋼板の製造方法。 Box annealing the hot-rolled steel sheet;
The method of manufacturing the steel plate for warm press forming of Claim 9 including the step of cold-rolling after the box annealing and manufacturing a cold-rolled steel plate. Ｚｎ系めっきまたはＡｌ系めっきを行ってめっき鋼板を製造する段階をさらに含む、請求項９または１０に記載の温間プレス成形用鋼板の製造方法。   The manufacturing method of the steel plate for warm press forming of Claim 9 or 10 which further includes the step which manufactures a plated steel plate by performing Zn type plating or Al type plating. 重量％で、Ｃ：０．０１〜０．５％、Ｓｉ：３．０％以下（０は除く）、Ｍｎ：３〜１５％、Ｐ：０．０００１〜０．１％、Ｓ：０．０００１〜０．０３％、Ａｌ：３．０％以下（０は除く）、Ｎ：０．０３％以下（０は除く）、Ｆｅ及び不可避な不純物を含み、
温間プレス成形及び冷却後の微細組織は、残留オーステナイトを体積分率で５〜５０％含み、残りはフェライト、マルテンサイト、焼戻マルテンサイト及びベイナイトのうち１種以上である、温間プレス成形部材。 C: 0.01 to 0.5%, Si: 3.0% or less (excluding 0), Mn: 3 to 15%, P: 0.0001 to 0.1%, S: 0.005% by weight. 0001 to 0.03%, Al: 3.0% or less (excluding 0), N: 0.03% or less (excluding 0), Fe and unavoidable impurities,
The microstructure after warm press forming and cooling contains 5 to 50% of retained austenite in volume fraction, and the rest is one or more of ferrite, martensite, tempered martensite and bainite. Element. 前記温間プレス成形部材の引張強度は１０００ＭＰａ以上、延伸率は１０％以上である、請求項１２に記載の温間プレス成形部材。   The warm press-molded member according to claim 12, wherein the warm press-formed member has a tensile strength of 1000 MPa or more and a stretching ratio of 10% or more. 重量％で、Ｃ：０．０１〜０．５％、Ｓｉ：３．０％以下（０は除く）、Ｍｎ：３〜１５％、Ｐ：０．０００１〜０．１％、Ｓ：０．０００１〜０．０３％、Ａｌ：３．０％以下（０は除く）、Ｎ：０．０３％以下（０は除く）、Ｆｅ及び不可避な不純物を含む鋼板に温間プレス成形を行う段階と、
前記温間プレス成形後に冷却する段階
とを含み、
前記温間プレス成形は、１〜１０００℃／秒の昇温速度でＡｃ１〜Ａｃ３の温度範囲まで加熱し、前記加熱後に１〜１００００秒間温度を維持する熱処理を含む、温間プレス成形部材の製造方法。 C: 0.01 to 0.5%, Si: 3.0% or less (excluding 0), Mn: 3 to 15%, P: 0.0001 to 0.1%, S: 0.005% by weight. A step of performing warm press forming on a steel sheet containing 0001 to 0.03%, Al: 3.0% or less (excluding 0), N: 0.03% or less (excluding 0), Fe and inevitable impurities; ,
Cooling after the warm press forming,
The warm press forming includes a heat treatment in which the temperature is increased to a temperature range of Ac1 to Ac3 at a temperature rising rate of 1 to 1000 ° C./second, and the temperature is maintained for 1 to 10000 seconds after the heating. Method. 前記温間プレス成形は、前記熱処理後に成形するか、成形後に前記熱処理して行われる、請求項１４に記載の温間プレス成形部材の製造方法。   The method of manufacturing a warm press-formed member according to claim 14, wherein the warm press forming is performed after the heat treatment or after the heat treatment. 前記冷却は、１〜１０００℃／秒の冷却速度で行われる、請求項１４または１５に記載の温間プレス成形部材の製造方法。   The method for producing a warm press-formed member according to claim 14 or 15, wherein the cooling is performed at a cooling rate of 1 to 1000 ° C / second.
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