JP4288138B2 - Steel sheet for hot forming - Google Patents
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- JP4288138B2 JP4288138B2 JP2003375181A JP2003375181A JP4288138B2 JP 4288138 B2 JP4288138 B2 JP 4288138B2 JP 2003375181 A JP2003375181 A JP 2003375181A JP 2003375181 A JP2003375181 A JP 2003375181A JP 4288138 B2 JP4288138 B2 JP 4288138B2
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- 229910000831 Steel Inorganic materials 0.000 title claims description 40
- 239000010959 steel Substances 0.000 title claims description 40
- 238000007747 plating Methods 0.000 claims description 37
- 230000003111 delayed effect Effects 0.000 claims description 21
- 229910052782 aluminium Inorganic materials 0.000 claims description 11
- 229910052749 magnesium Inorganic materials 0.000 claims description 10
- 229910052759 nickel Inorganic materials 0.000 claims description 10
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims description 9
- 229910052787 antimony Inorganic materials 0.000 claims description 9
- 229910052785 arsenic Inorganic materials 0.000 claims description 9
- 229910052791 calcium Inorganic materials 0.000 claims description 9
- 229910052761 rare earth metal Inorganic materials 0.000 claims description 9
- 229910052727 yttrium Inorganic materials 0.000 claims description 9
- 239000012535 impurity Substances 0.000 claims description 8
- 238000000465 moulding Methods 0.000 claims description 8
- 229910052718 tin Inorganic materials 0.000 claims description 8
- 239000000126 substance Substances 0.000 claims description 6
- 229910052719 titanium Inorganic materials 0.000 claims description 6
- 239000011701 zinc Substances 0.000 claims description 5
- 229910052750 molybdenum Inorganic materials 0.000 claims description 4
- 229910052758 niobium Inorganic materials 0.000 claims description 4
- 229910052720 vanadium Inorganic materials 0.000 claims description 4
- 229910052725 zinc Inorganic materials 0.000 claims description 4
- 229910052726 zirconium Inorganic materials 0.000 claims description 4
- HCHKCACWOHOZIP-UHFFFAOYSA-N Zinc Chemical compound [Zn] HCHKCACWOHOZIP-UHFFFAOYSA-N 0.000 claims description 3
- 229910052799 carbon Inorganic materials 0.000 claims description 3
- 239000000203 mixture Substances 0.000 claims description 3
- 229910052757 nitrogen Inorganic materials 0.000 claims description 3
- 238000000034 method Methods 0.000 description 13
- 230000000694 effects Effects 0.000 description 11
- 238000001816 cooling Methods 0.000 description 7
- 238000002474 experimental method Methods 0.000 description 7
- 239000000463 material Substances 0.000 description 7
- 229910052802 copper Inorganic materials 0.000 description 6
- 229910001566 austenite Inorganic materials 0.000 description 5
- 238000011156 evaluation Methods 0.000 description 5
- 238000010438 heat treatment Methods 0.000 description 5
- FJMNNXLGOUYVHO-UHFFFAOYSA-N aluminum zinc Chemical compound [Al].[Zn] FJMNNXLGOUYVHO-UHFFFAOYSA-N 0.000 description 4
- 230000000052 comparative effect Effects 0.000 description 4
- 230000008569 process Effects 0.000 description 4
- UCKMPCXJQFINFW-UHFFFAOYSA-N Sulphide Chemical compound [S-2] UCKMPCXJQFINFW-UHFFFAOYSA-N 0.000 description 3
- 239000010960 cold rolled steel Substances 0.000 description 3
- 238000005336 cracking Methods 0.000 description 3
- 230000007423 decrease Effects 0.000 description 3
- 230000003247 decreasing effect Effects 0.000 description 3
- 238000009863 impact test Methods 0.000 description 3
- 238000004519 manufacturing process Methods 0.000 description 3
- 229910052751 metal Inorganic materials 0.000 description 3
- 239000002184 metal Substances 0.000 description 3
- 230000001105 regulatory effect Effects 0.000 description 3
- 230000009466 transformation Effects 0.000 description 3
- 230000002411 adverse Effects 0.000 description 2
- 238000005097 cold rolling Methods 0.000 description 2
- 238000007796 conventional method Methods 0.000 description 2
- 230000006872 improvement Effects 0.000 description 2
- 229910000734 martensite Inorganic materials 0.000 description 2
- 230000001590 oxidative effect Effects 0.000 description 2
- 229910052698 phosphorus Inorganic materials 0.000 description 2
- 229920006395 saturated elastomer Polymers 0.000 description 2
- 229910052710 silicon Inorganic materials 0.000 description 2
- 238000012360 testing method Methods 0.000 description 2
- 238000003483 aging Methods 0.000 description 1
- 229910045601 alloy Inorganic materials 0.000 description 1
- 239000000956 alloy Substances 0.000 description 1
- 238000005275 alloying Methods 0.000 description 1
- 238000000137 annealing Methods 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 150000001875 compounds Chemical class 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 230000006866 deterioration Effects 0.000 description 1
- 230000002542 deteriorative effect Effects 0.000 description 1
- 230000007613 environmental effect Effects 0.000 description 1
- 239000006260 foam Substances 0.000 description 1
- 239000000446 fuel Substances 0.000 description 1
- 238000005246 galvanizing Methods 0.000 description 1
- 238000005244 galvannealing Methods 0.000 description 1
- 238000007542 hardness measurement Methods 0.000 description 1
- 238000005098 hot rolling Methods 0.000 description 1
- 150000002484 inorganic compounds Chemical class 0.000 description 1
- 239000011159 matrix material Substances 0.000 description 1
- 230000007246 mechanism Effects 0.000 description 1
- 150000001247 metal acetylides Chemical class 0.000 description 1
- 150000004767 nitrides Chemical class 0.000 description 1
- 238000005457 optimization Methods 0.000 description 1
- 150000002894 organic compounds Chemical class 0.000 description 1
- 238000005554 pickling Methods 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 230000001376 precipitating effect Effects 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 238000003825 pressing Methods 0.000 description 1
- 239000000047 product Substances 0.000 description 1
- 238000010791 quenching Methods 0.000 description 1
- 230000000171 quenching effect Effects 0.000 description 1
- 238000003303 reheating Methods 0.000 description 1
- 230000003014 reinforcing effect Effects 0.000 description 1
- 238000005096 rolling process Methods 0.000 description 1
- 230000035945 sensitivity Effects 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 238000005728 strengthening Methods 0.000 description 1
- 230000001629 suppression Effects 0.000 description 1
- 238000004381 surface treatment Methods 0.000 description 1
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 1
- 239000013585 weight reducing agent Substances 0.000 description 1
- 238000004804 winding Methods 0.000 description 1
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- Shaping Metal By Deep-Drawing, Or The Like (AREA)
Description
本発明は、自動車の構造部材・補強部材に使用されるような強度が必要とされる部材に関し、特に高温成形後の衝撃特性と遅れ破壊特性に優れた熱間成形加工用の鋼板に関するものである。 The present invention relates to a member that requires strength such as that used for structural members and reinforcing members of automobiles, and more particularly to a steel sheet for hot forming with excellent impact characteristics and delayed fracture characteristics after high temperature forming. is there.
地球環境問題に端を発する自動車の燃費向上対策の一つとして車体の軽量化が進められており、自動車に使用される鋼板をできるだけ高強度化することが必要となる。しかし、自動車の軽量化のために一般に鋼板を高強度化していくと伸びやｒ値が低下し、成形性が劣化していく。
このような課題を解決するために、温間で成形し、その際の熱を利用して強度上昇を図る技術が、特許文献１に開示されている。この技術では、鋼中成分を適切に制御し、２００〜８５０℃の温度域で保持・成形加工し、この温度域での析出強化を利用して強度を上昇させることを狙っている。
As one of the measures to improve the fuel efficiency of automobiles that originated from global environmental problems, the weight reduction of the vehicle body has been promoted, and it is necessary to increase the strength of steel plates used in automobiles as much as possible. However, in general, when the strength of a steel plate is increased in order to reduce the weight of an automobile, the elongation and the r value decrease, and the formability deteriorates.
In order to solve such a problem, Japanese Patent Application Laid-Open No. H10-228561 discloses a technique for forming the article warmly and using the heat at that time to increase the strength. This technique aims to appropriately control the components in the steel, hold and form in a temperature range of 200 to 850 ° C., and increase the strength using precipitation strengthening in this temperature range.
また特許文献２では、プレス成形精度を向上させる目的で温間プレス時での降伏強度を低く、常温での降伏強度を高くする高強度鋼板が提案されている。しかしながら、これらの技術では得られる強度に限度がある可能性がある。
より高強度を得る目的で、成形後に高温のオーステナイト単相域に加熱し、その後の冷却過程で硬質の相に変態させる技術が特許文献３に開示されている。この技術により高強度で寸法精度の良い部品を得ることができる。
For the purpose of obtaining higher strength, Patent Document 3 discloses a technique in which a high-temperature austenite single-phase region is heated after molding and transformed into a hard phase in the subsequent cooling process. With this technique, it is possible to obtain a component having high strength and good dimensional accuracy.
一方、部品が高強度化する際の課題としては衝撃特性（靭性）と遅れ破壊特性がある。一般的に鋼材が高強度化すると靭性は低下し、また特開平７−１４６２２５号公報に示されるように遅れ破壊特性も低下する。そのため、車体衝突安全基準を満たすためには更なる衝撃特性と遅れ破壊特性の向上が望まれる。
本発明は上記の特性を向上させた高強度部品を得るための鋼板を提供するものである。
On the other hand, there are impact characteristics (toughness) and delayed fracture characteristics as problems when the parts are strengthened. Generally, when the strength of steel is increased, the toughness is lowered, and the delayed fracture characteristics are also lowered as disclosed in JP-A-7-146225. Therefore, in order to satisfy the vehicle body collision safety standard, further improvement in impact characteristics and delayed fracture characteristics is desired.
The present invention provides a steel plate for obtaining a high-strength part with improved properties.
本発明者らは上記課題を解決するために基礎的な検討を実施した。その結果、鋼板の化学成分の適正化として、Ｎｉ，Ｃｕ，Ｓｎ等の添加、Ｃａ，Ｍｇ，Ｙ，Ａｓ，Ｓｂ，ＲＥＭ等の硫化物形成元素の添加により衝撃特性と遅れ破壊特性が向上することを見出した。 The present inventors conducted basic studies to solve the above problems. As a result, as the optimization of chemical composition of the steel sheet, Ni, Cu, addition of Sn or the like, Ca, Mg, Y, As, Sb, impact properties and delayed fracture properties by the addition of sulfide forming elements REM such improved I found out.
かかる向上の詳細な機構については明確ではないが、以下のようなことが考えられる。 Ｃｕ，Ｎｉ，Ｃは熱間圧延でのスラブ再加熱中や焼鈍工程で表面に濃化していく。これらの元素は鋼板表面の酸化物形成を抑制することに影響を及ぼし、靭性、遅れ破壊などの破壊の起点を減少させる効果が考えられる。また、上記の硫化物形成元素の添加は、本発明鋼の主な硫化物であるＭｎＳの形状を破壊に影響が少ない形状に変化させることが考えられる。 Although the detailed mechanism of the improvement is not clear, the following can be considered. Cu, Ni, and C are concentrated on the surface during reheating of the slab in hot rolling and in the annealing process. These elements affect the suppression of oxide formation on the surface of the steel sheet, and are considered to have an effect of reducing the starting point of fracture such as toughness and delayed fracture. In addition, it is conceivable that the addition of the sulfide-forming element changes the shape of MnS, which is the main sulfide of the steel of the present invention, to a shape that has little influence on fracture.
すなわち、本発明の要旨とするところは下記のとおりである。
（１） 質量％で、
Ｃ ：０．１〜０．５５％、 Ｓｉ：１．０％以下、
Ｍｎ：０．２〜３％、 Ａｌ：０．００５〜０．１％、
Ｓ ：０．０２％以下、 Ｐ ：０．０３％以下、
Ｃｒ：０．０ｌ〜１％、
さらに、
Ｓｎを必須とし、Ｎｉ（ゼロを含む），Ｃｕ（ゼロを含む）の１種または２種を含 み、Ｓｎ，Ｎｉ，Ｃｕの合計が０．００５〜２％、
Ｃａ，Ｍｇ，Ｙ，Ａｓ，Ｓｂ，ＲＥＭの１種または２種以上の合計が０．０００５〜
０．０５％、
残部Ｆｅ並びに不可避的不純物及び／又は付随的不純物からなることを特徴とする熱間成形加工後の衝撃特性・遅れ破壊特性に優れた熱間成形加工用鋼板。
（２） 質量％で、
Ｃ ：０．１〜０．５５％、 Ｓｉ：１．０％以下、
Ｍｎ：０．２〜３％、 Ａｌ：０．００５〜０．１％、
Ｓ ：０．０２％以下、 Ｐ ：０．０３％以下、
Ｃｒ：０．０ｌ〜１％、 Ｂ ：０．０００２〜０．００５％、
Ｃ，Ｎ，Ｔｉ量が３．９９×（Ｃ−０．１）≧Ｔｉ−３．４２×Ｎ≧０．００１を満 足し、さらに、
Ｓｎを必須とし、Ｎｉ（ゼロを含む），Ｃｕ（ゼロを含む）の１種または２種を含 み、Ｓｎ，Ｎｉ，Ｃｕの合計が０．００５〜２％、
Ｃａ，Ｍｇ，Ｙ，Ａｓ，Ｓｂ，ＲＥＭの１種または２種以上の合計が０．０００５〜
０．０５％、
残部Ｆｅ並びに不可避的不純物及び／又は付随的不純物からなることを特徴とする熱間成形加工後の衝撃特性・遅れ破壊特性に優れた熱間成形加工用鋼板。
That is, the gist of the present invention is as follows.
(1) In mass%,
C: 0.1 to 0.55%, Si: 1.0% or less,
Mn: 0.2-3%, Al: 0.005-0.1%,
S: 0.02% or less, P: 0.03% or less,
Cr: 0.01 to 1%,
further,
The Sn as essential, Ni (including zero), viewed contains one or two of Cu (including zero), Sn, Ni, total of Cu from 0.005 to 2%,
The total of one or more of Ca, Mg, Y, As, Sb, and REM is 0.0005
0.05%,
A steel sheet for hot forming having excellent impact characteristics and delayed fracture characteristics after hot forming, characterized by comprising balance Fe and inevitable impurities and / or incidental impurities.
(2) By mass%
C: 0.1 to 0.55%, Si: 1.0% or less,
Mn: 0.2-3%, Al: 0.005-0.1%,
S: 0.02% or less, P: 0.03% or less,
Cr: 0.01 to 1%, B: 0.0002 to 0.005%,
The amount of C, N, and Ti satisfies 3.99 × (C−0.1) ≧ Ti−3.42 × N ≧ 0.001 ,
The Sn as essential, Ni (including zero), viewed contains one or two of Cu (including zero), Sn, Ni, total of Cu from 0.005 to 2%,
The total of one or more of Ca, Mg, Y, As, Sb, and REM is 0.0005
0.05%,
A steel sheet for hot forming having excellent impact characteristics and delayed fracture characteristics after hot forming, characterized by comprising balance Fe and inevitable impurities and / or incidental impurities.
（３） 付随的成分として、質量％で更に、
Ｔｉ，Ｎｂ，Ｚｒ，Ｍｏ，Ｖの１種または２種以上の合計が０．００５％以上、かつ、Ｃ−１２×（Ｔｉ／４８＋Ｎｂ／９３＋Ｚｒ／９１＋Ｍｏ／９６＋Ｖ／５１）≧０．１
を満足するように含有することを特徴とする前項（１）又は（２）に記載の熱間成形加工後の衝撃特性・遅れ破壊特性に優れた熱間成形加工用鋼板。
（４） 前項（１）乃至（３）のいずれか１項に記載の化学成分を有する鋼板に、アルミめっき、亜鉛・アルミめっき、亜鉛めっきを施したことを特徴とする熱間成形加工後の衝撃特性・遅れ破壊特性とめっき密着性に優れた熱間成形加工用鋼板。
(3) As an incidental component, further in mass%,
The total of one or more of Ti, Nb, Zr, Mo, V is 0.005% or more, and C-12 × (Ti / 48 + Nb / 93 + Zr / 91 + Mo / 96 + V / 51) ≧ 0.1
The steel sheet for hot forming which is excellent in impact characteristics and delayed fracture characteristics after hot forming as described in the above item (1) or (2), wherein
( 4 ) The steel sheet having the chemical component according to any one of (1) to ( 3 ) is subjected to aluminum plating, zinc / aluminum plating, galvanization, and after hot forming Steel sheet for hot forming with excellent impact characteristics, delayed fracture characteristics and plating adhesion.
本発明鋼は、自動車部品の構造部材に使用され、熱間成型加工後の高強度でかつ衝撃特性および遅れ破壊特性に優れ、表面処理を施した場合にはめっき密着性も優れた部品を提供することができ、社会的貢献が大きいものである。 The steel of the present invention is used for structural parts of automobile parts and provides parts with high strength after hot forming, excellent impact characteristics and delayed fracture characteristics, and excellent plating adhesion when subjected to surface treatment. It can make a great social contribution.
本発明においては、特定の化学組成を有する熱延素材あるいは冷延素材を用いるが、その熱延素材あるいは冷延素材を製造する手段は特に限定されない。また、熱間成形加工とは、Ａｃ3 変態点以上のオーステナイト領域に加熱後、Ａｃ3 変態点以上の温度で成形加工（例えばプレス加工）を開始し、加工と同時に金型で抜熱することにより急速冷却し、マルテンサイト変態させて硬化させる加工をいう。 In the present invention, a hot-rolled material or a cold-rolled material having a specific chemical composition is used, but the means for producing the hot-rolled material or the cold-rolled material is not particularly limited. Also, hot forming is rapid by heating to the austenite region above the Ac3 transformation point and then starting molding (for example, press working) at a temperature above the Ac3 transformation point. It refers to a process of cooling and hardening by martensite transformation.
次に、鋼板の化学成分について説明する。
Ｃは冷却後の組織をマルテンサイトとして材質を確保するために添加する元素であり、強度１０００ＭＰａ以上を確保するためには０．１％以上添加する必要がある。ところが、添加量が多すぎると、衝撃変形時の強度確保が困難となるため、その上限を０．５５％とした。
Next, chemical components of the steel plate will be described.
C is an element added to secure the material with the cooled structure as martensite. It is necessary to add 0.1% or more in order to secure the strength of 1000 MPa or more. However, if the addition amount is too large, it is difficult to ensure the strength during impact deformation, so the upper limit was made 0.55%.
Ｓｉは固溶強化型の合金元素であり、強度を確保するために必要であるが、１％を超えると表面スケールの問題が生じる。このためＳｉは１％以下に規定した。また、鋼板表面にメッキ処理を行う場合は、Ｓｉの添加量が多いとメッキ性が劣化するため、上限を０．５％とすることが好ましい。更に好ましくは０．０１〜０．５％の範囲である。 Si is a solid solution strengthened alloy element and is necessary to ensure strength, but if it exceeds 1%, a problem of surface scale occurs. For this reason, Si was specified to be 1% or less. In addition, when plating is performed on the surface of the steel sheet, if the amount of Si added is large, the plateability deteriorates, so the upper limit is preferably set to 0.5%. More preferably, it is 0.01 to 0.5% of range.
Ｍｎは強度及び焼入れ性を向上させる元素であり、０．２％未満では焼入れ時の強度を十分に得られず、また３％を超えて添加しても効果が飽和するため、Ｍｎは０．２〜３％の範囲に規定した。 Mn is an element that improves the strength and hardenability. If it is less than 0.2%, the strength at the time of quenching cannot be sufficiently obtained, and even if added over 3%, the effect is saturated, so Mn is 0.2%. It was specified in the range of 2-3%.
Ａｌは溶鋼の脱酸材として使われる必要な元素で、またＮを固定する元素でもあり、その量は結晶粒径や機械的性質に大きな影響を及ぼす。このような効果を有するためには０．００５％以上の含有量が必要であるが、０．１％を超えると非金属介在物が多くなり製品に表面疵が発生しやすくなる。このためＡｌは０．００５〜０．１％の範囲に規定した。 Al is a necessary element used as a deoxidizer for molten steel, and is also an element that fixes N, and its amount has a great influence on the crystal grain size and mechanical properties. In order to have such an effect, a content of 0.005% or more is necessary. However, if it exceeds 0.1%, nonmetallic inclusions increase and surface defects are likely to occur in the product. For this reason, Al was specified in the range of 0.005 to 0.1%.
Ｓは鋼中の非金属介在物に影響し、加工性を劣化させるとともに、靭性劣化、異方性及び再熱割れ感受性の増大の原因となる。このためＳは０．０２％以下に規定した。より好ましくは０．０１％以下である。また、Ｓを０．００５％以下に規制することにより、衝撃特性が飛躍的に向上する。 S affects non-metallic inclusions in the steel and deteriorates workability, and causes toughness deterioration, anisotropy and reheat cracking sensitivity. For this reason, S was specified to 0.02% or less. More preferably, it is 0.01% or less. Moreover, by restricting S to 0.005% or less, impact characteristics are dramatically improved.
Ｐは溶接割れ性および靭性に悪影響を及ぼす元素であるため、Ｐは０．０３％以下に規制した。より好ましくは０．０２％以下である。また更に好ましくは０．０１５％以下である。 Since P is an element that adversely affects weld cracking and toughness, P is regulated to 0.03% or less. More preferably, it is 0.02% or less. More preferably, it is 0.015% or less.
Ｃｒは焼入れ性を向上させる元素であり、またマトリックス中へＭ23Ｃ6 型炭化物を析出させる効果を有し、強度を高めるとともに、炭化物を微細化する作用を有する。０．０１％未満ではこれらの効果が十分期待できず、また１％を超えると降伏強度が過度に上昇する傾向にあるため、Ｃｒは０．０１〜１％の範囲が望ましい。より望ましくは０．０５〜１％である。 Cr is an element that improves hardenability, and has the effect of precipitating M 23 C 6 type carbide in the matrix, and has the effect of increasing the strength and miniaturizing the carbide. If it is less than 0.01%, these effects cannot be expected sufficiently, and if it exceeds 1%, the yield strength tends to increase excessively, so Cr is desirably in the range of 0.01 to 1%. More desirably, it is 0.05 to 1%.
Ｎｉ，Ｃｕ，Ｓｎは鋼板表面近傍の酸化物に影響を及ぼし、衝撃特性と遅れ破壊特性を向上させると考えられるため、これらの１種または２種以上を合計で０．００５％以上添加する必要がある。しかし過度の添加は加工性を劣化させるため、その上限を２％に規制した。 Ni, Cu and Sn affect the oxide near the surface of the steel sheet, and are thought to improve impact characteristics and delayed fracture characteristics. Therefore, it is necessary to add one or more of these in a total amount of 0.005% or more. There is. However, excessive addition deteriorates workability, so the upper limit was regulated to 2%.
Ｃａ，Ｍｇ，Ｙ，Ａｓ，Ｓｂ，ＲＥＭは、主な硫化物であるＭｎＳの形状を変化させて衝撃特性と遅れ破壊特性を向上させると考えられるため、これらの１種または２種以上の合計が０．０００５％以上の添加が必要である。しかし過度の添加は加工性を劣化させるため、その上限を０．０５％以下に規制した。 Since Ca, Mg, Y, As, Sb, and REM are considered to improve the impact characteristics and delayed fracture characteristics by changing the shape of MnS, which is the main sulfide, the total of one or more of these Must be added in an amount of 0.0005% or more. However, excessive addition deteriorates workability, so the upper limit was regulated to 0.05% or less.
Ｂはプレス成形中あるいはプレス成形後の冷却での焼入れ性を向上させるために添加するが、この効果を発揮させるためには０．０００２％以上の添加が必要である。しかしながら、この添加量がむやみに増加すると熱間での割れの懸念があることや、その効果が飽和するため、その上限は０．００５０％とする。 B is added in order to improve the hardenability during press molding or cooling after press molding, but 0.0002% or more must be added to exhibit this effect. However, if this amount increases excessively, there is a risk of hot cracking, and the effect is saturated, so the upper limit is made 0.0050%.
ＴｉはＢの効果を有効に発揮させるため、Ｂと化合物を生成するＮを固着する目的で添加する。この効果を発揮させるためには、（Ｔｉ−３．４２×Ｎ）が０．００１％以上必要であるが、Ｔｉ量がむやみに増加するとＴｉと結合していないＣ量が減少し、冷却後に十分な強度が得られなくなるため、その上限として、Ｔと結合していないＣ量が０．１％以上確保できるＴｉ当量、すなわち３．９９×（Ｃ−０．１）％とした。一方、Ｂを添加しない場合はＴｉも特に添加する必要はない。 Ti is added for the purpose of fixing B and N which forms a compound in order to effectively exhibit the effect of B. In order to exhibit this effect, (Ti-3.42 × N) is required to be 0.001% or more. However, if the Ti amount increases excessively, the amount of C not bonded to Ti decreases, and after cooling. Since sufficient strength cannot be obtained, the upper limit is set to Ti equivalent that can secure 0.1% or more of C not bonded to T, that is, 3.99 × (C−0.1)%. On the other hand, when B is not added, Ti need not be particularly added.
Ｔｉ，Ｎｂ，Ｚｒ，Ｍｏ，Ｖは炭化物を析出し、強度を向上できるので、これらを合計で０．００５％以上添加しても良い。しかしこれらの元素がむやみに増加すると、これらの元素と結合していないＣ量が減少し、冷却後に十分な強度が得られなくなるため、Ｃ−１２×（Ｔｉ／４８＋Ｎｂ／９３＋Ｚｒ／９１＋Ｍｏ／９６＋Ｖ／５１）≧０．１を満足するように含有させる必要がある。 Ti, Nb, Zr, Mo, and V precipitate carbides and can improve the strength, so these may be added in a total amount of 0.005% or more. However, when these elements increase excessively, the amount of C not bonded to these elements decreases, and sufficient strength cannot be obtained after cooling. Therefore, C-12 × (Ti / 48 + Nb / 93 + Zr / 91 + Mo / 96 + V / 51) It is necessary to contain so as to satisfy ≧ 0.1.
Ｎについては特に規制しないが、０．０１％を超えると窒化物の粗大化及び固溶Ｎによる時効硬化により、靭性が劣化する傾向がみられる。このためＮは０．０１％以下の含有が望ましい。 N is not particularly restricted, but if it exceeds 0.01%, the toughness tends to deteriorate due to coarsening of nitride and age hardening due to solute N. Therefore, the N content is desirably 0.01% or less.
Ｏについても特に規制しないが、過度の添加は靭性に悪影響を及ぼす酸化物の生成の原因となるとともに、疲労破壊の起点となる酸化物を生成するため、０．０１５％以下の含有が望ましい。 Although there is no particular restriction on O, excessive addition causes generation of an oxide that adversely affects toughness and generates an oxide that becomes a starting point of fatigue fracture. Therefore, the content is preferably 0.015% or less.
以上の成分の鋼板にアルミめっき、アルミ・亜鉛めっき、亜鉛めっきを施しても良い。その製造方法は酸洗、冷間圧延は常法でよく、その後アルミめっき工程あるいはアルミ−亜鉛めっき工程、亜鉛めっきについても常法で問題ない。つまり、アルミめっきであれば浴中Ｓｉ濃度は５〜１２％が適しており、アルミ−亜鉛めっきでは浴中Ｚｎ濃度は４０〜５０％が適している。また、アルミめっき層中にＭｇやＺｎが混在しても、アルミ−亜鉛めっき層中にＭｇが混在しても特に問題なく同様の特性の鋼板を製造することができる。 The steel plate having the above components may be subjected to aluminum plating, aluminum / zinc plating, or galvanization. As for the production method, pickling and cold rolling may be performed by a conventional method, and thereafter, the aluminum plating step, the aluminum-zinc plating step, and the galvanizing may be performed by a conventional method. That is, 5 to 12% of the Si concentration in the bath is suitable for aluminum plating, and 40 to 50% of the Zn concentration in the bath is suitable for aluminum-zinc plating. Even if Mg or Zn is mixed in the aluminum plating layer or Mg is mixed in the aluminum-zinc plating layer, a steel plate having the same characteristics can be manufactured without any particular problem.
なお、めっき工程における雰囲気については、無酸化炉を有する連続式めっき設備でも、無酸化炉を有しない連続式めっき設備でも、通常の条件とすることでめっき可能であり、本発明鋼板だけ特別な制御を必要としないことから生産性を阻害することもない。また、亜鉛めっき方法であれば、溶融亜鉛めっき、電気亜鉛めっき、合金化溶融亜鉛めっきなどいかなる方法をとっても良い。 As for the atmosphere in the plating process, it is possible to carry out plating under normal conditions even in a continuous plating facility having a non-oxidizing furnace or a continuous plating facility not having a non-oxidizing furnace. Since control is not required, productivity is not hindered. Moreover, as long as it is a galvanization method, what kind of methods, such as hot dip galvanization, electrogalvanization, and galvannealing, may be taken.
以上の製造条件ではめっき前に鋼板表面に金属プレめっきを施していないが、ＮｉプレめっきやＦｅプレめっき、その他めっき性を向上させる金属プレめっきを施しても特に問題は無い。また、めっき層表面に異種の金属めっきや無機系、有機系化合物の皮膜などを付与しても特に問題は無い。さらに、本発明の化学成分の制限であるＮｉ，Ｃｕ，Ｓｎの添加は鋼板表面の酸化物形態に影響を及ぼし、めっきの密着性を向上させる効果があり、熱間成形加工後のめっき密着性に優れた表面処理鋼板が製造できる。 Under the above manufacturing conditions, metal pre-plating is not performed on the surface of the steel plate before plating, but there is no particular problem even if Ni pre-plating, Fe pre-plating, or other metal pre-plating that improves plating properties is performed. Moreover, there is no particular problem even if different metal plating or a film of inorganic or organic compound is applied to the surface of the plating layer. Furthermore, the addition of Ni, Cu, Sn, which is a limitation of the chemical components of the present invention, has an effect of affecting the oxide form on the surface of the steel sheet, improving the adhesion of the plating, and the plating adhesion after hot forming. It is possible to manufacture a surface-treated steel sheet that is excellent in quality.
表６に示す成分をべースとして、表７，８に示す元素を添加したスラブを鋳造した。また、表７，８中に示す成分をべ一スに、表９に示す元素を添加したスラブを鋳造した。
これらのスラブを１０５０〜１３５０℃に加熱し、熱間圧延にて仕上温度８００〜９００℃、巻取温度４５０〜６８０℃で板厚４mmの熱延鋼板とした。また、一部の熱延鋼板を冷間圧延により板厚１．２mmの冷延鋼板とした。また、その冷延板の一部に溶融アルミめっき、溶融アルミ−亜鉛めっき、合金化溶融亜鉛めっきを施した。
Using the components shown in Table 6 as a base, slabs to which the elements shown in Tables 7 and 8 were added were cast. Further, slabs with the elements shown in Table 9 added thereto based on the components shown in Tables 7 and 8 were cast.
These slabs were heated to 1050 to 1350 ° C. and hot rolled into hot rolled steel sheets having a finishing temperature of 800 to 900 ° C. and a winding temperature of 450 to 680 ° C. and a thickness of 4 mm. Some hot-rolled steel sheets were cold-rolled steel sheets having a thickness of 1.2 mm by cold rolling. Moreover, hot-dip aluminum plating, hot-dip aluminum-zinc plating, and alloying hot-dip galvanization were performed on a part of the cold-rolled sheet.
その後、それらの冷延鋼板、表面処理鋼板を炉加熱によりＡｃ3 点以上である９５０℃のオーステナイト領域に加熱した後、Ａｃ3 点以上である９００℃から水冷式金型を有するプレス機にてハットフォーム成形加工を行った。成形時間を約１秒とし、成形完了５秒間はプレス金型をそのままの状態にして金型による冷却を行った。冷却後の温度は２００℃以下であった。 Thereafter, the cold-rolled steel sheet and the surface-treated steel sheet are heated in an austenite region of 950 ° C., which is higher than the Ac 3 point, by furnace heating, and then the hat foam is formed on a press machine having a water-cooled mold from 900 ° C., which is higher than the Ac 3 point Molding was performed. The molding time was about 1 second, and for 5 seconds after the molding was completed, the press mold was left as it was and cooling with the mold was performed. The temperature after cooling was 200 ° C. or lower.
成形された鋼板について、冷延鋼板の圧延方向に垂直な断面をビッカース硬度計にて硬度測定を実施した。評価は比較鋼の硬度を基準として、その増加率で行った。凡例を表１に示す。
また、更に板厚４mmの熱延鋼板を炉加熱によりＡｃ3 点以上である９５０℃のオーステナイト領域に加熱した後、９００℃から水冷した素材を用いて衝撃試験を実施した。衝撃試験方法はＪＩＳ Ｚ ２２０２に示されるＶノッチ、幅２．５mmのサブサイズ試験片を用い、ＪＩＳ Ｚ ２２４２の方法にて試験温度４０℃で行った。評価は比較鋼の吸収エネルギーを基準にその増加率で行った。凡例を表２に示す。
About the shape | molded steel plate, the hardness measurement was implemented in the cross section perpendicular | vertical to the rolling direction of a cold-rolled steel plate with a Vickers hardness tester. The evaluation was performed at an increasing rate based on the hardness of the comparative steel. The legend is shown in Table 1.
Further, after a hot rolled steel sheet having a thickness of 4 mm was heated in an austenite region at 950 ° C., which is higher than the Ac 3 point, by furnace heating, an impact test was performed using a material cooled from 900 ° C. to water. The impact test method was a V-notch shown in JIS Z 2202 and a sub-size test piece with a width of 2.5 mm, and the test temperature was 40 ° C. according to the method of JIS Z 2242. Evaluation was performed at the rate of increase based on the absorbed energy of the comparative steel. The legend is shown in Table 2.
遅れ破壊特性は特開平７−１４６２２５号公報に記載の方法を用い、比較鋼に対する割れ発生時間の増加率で評価した。凡例を表３に示す。
加工性とめっき密着性の評価のため、炉加熱によりＡｃ3 点以上である９５０℃のオーステナイト領域に加熱した後、炉から取り出し８００℃以上の温度で直径３０mmの球頭パンチでインパクト試験を行った。加工性の評価は割れの発生にて評価した。また、めっき密着性評価は目視で比較材とのめっき剥離状態を比較して行った。加工性の評価の凡例を表４、めっき密着性の評価の凡例を表５にそれぞれ示す。
Delayed fracture characteristics were evaluated using the method described in JP-A-7-146225 and the rate of increase in crack generation time with respect to the comparative steel. The legend is shown in Table 3.
In order to evaluate workability and plating adhesion, after heating to an austenite region of 950 ° C., which is higher than the Ac 3 point, by furnace heating, it was removed from the furnace and subjected to an impact test with a ball head punch having a diameter of 30 mm at a temperature of 800 ° C. . The workability was evaluated based on the occurrence of cracks. Moreover, plating adhesion evaluation was performed by visually comparing the plating peeling state with the comparative material. A legend for evaluation of workability is shown in Table 4, and a legend for evaluation of plating adhesion is shown in Table 5, respectively.
実験番号１，１３，２５，３７，４９は、Ｎｉ，Ｃｕ，Ｓｎの合計と、Ｃａ，Ｍｇ，Ｙ，Ａｓ，Ｓｂ，ＲＥＭの合計が制限以下であったため、衝撃特性、遅れ破壊特性、めっき密着性が向上しなかった。
実験番号２，１４，２６，３８，５０は、Ｃａ，Ｍｇ，Ｙ，Ａｓ，Ｓｂ，ＲＥＭの合計が制限以下であったため、衝撃特性、遅れ破壊特性が向上しなかった。
実験番号６，１８，３０，４２，５４，６６は、Ｎｉ，Ｃｕ，Ｓｎの合計が制限以上であったため、加工性が低下した。
実験番号１２，２４，３６，４８，６０は、Ｃａ，Ｍｇ，Ｙ，Ａｓ，Ｓｂ，ＲＥＭの合計が制限以上であったため，加工性が低下した。
In Experiment Nos. 1, 13, 25, 37, and 49, the total of Ni, Cu, and Sn and the total of Ca, Mg, Y, As, Sb, and REM were less than the limits, so impact characteristics, delayed fracture characteristics, plating Adhesion did not improve.
In Experiment Nos. 2, 14, 26, 38, and 50, since the total of Ca, Mg, Y, As, Sb, and REM was less than the limit, impact characteristics and delayed fracture characteristics were not improved.
In Experiment Nos. 6, 18, 30, 42, 54, and 66, the total of Ni, Cu, and Sn was more than the limit, so the workability decreased.
In Experiment Nos. 12, 24, 36, 48, and 60, the total of Ca, Mg, Y, As, Sb, and REM was more than the limit, so the workability was lowered.
実験番号６１〜７２はＣ量が制限以上であるため、加工性が低下した。
実験番号７８，８７，９６は、Ｔｉ，Ｎｂ，Ｚｒ，Ｍｏ，Ｖの添加量がＣ−１２×（Ｔｉ／４８＋Ｎｂ／９３＋Ｚｒ／９１＋Ｍｏ／９６＋Ｖ／５１）≧０．１の条件を満たさず、硬度が低下した。
その他の実験では本発明の制限内であるため、断面硬度や加工性が劣化することなく衝撃特性、遅れ破壊特性、めっき密着性が向上した。
In Experiment Nos. 61 to 72, the amount of C was more than the limit, so the workability decreased.
Experiment Nos. 78, 87, and 96 indicate that the addition amount of Ti, Nb, Zr, Mo, and V does not satisfy the condition of C-12 × (Ti / 48 + Nb / 93 + Zr / 91 + Mo / 96 + V / 51) ≧ 0.1 and the hardness Decreased .
In other experiments, the impact characteristics, delayed fracture characteristics, and plating adhesion were improved without deteriorating the cross-sectional hardness and workability because they were within the limits of the present invention.
Claims (4)
Ｃ ：０．１〜０．５５％、
Ｓｉ：１．０％以下、
Ｍｎ：０．２〜３％、
Ａｌ：０．００５〜０．１％、
Ｓ ：０．０２％以下、
Ｐ ：０．０３％以下、
Ｃｒ：０．０ｌ〜１％、
さらに、
Ｓｎを必須とし、Ｎｉ（ゼロを含む），Ｃｕ（ゼロを含む）の１種または２種を含 み、Ｓｎ，Ｎｉ，Ｃｕの合計が０．００５〜２％、
Ｃａ，Ｍｇ，Ｙ，Ａｓ，Ｓｂ，ＲＥＭの１種または２種以上の合計が０．０００５〜
０．０５％、
残部Ｆｅ及び不可避的不純物（付随的不純物を含む）からなることを特徴とする熱間成形加工後の衝撃特性・遅れ破壊特性に優れた熱間成形加工用鋼板。 % By mass
C: 0.1 to 0.55%,
Si: 1.0% or less,
Mn: 0.2-3%,
Al: 0.005 to 0.1%,
S: 0.02% or less,
P: 0.03% or less,
Cr: 0.01 to 1%,
further,
The Sn as essential, Ni (including zero), viewed contains one or two of Cu (including zero), Sn, Ni, total of Cu from 0.005 to 2%,
The total of one or more of Ca, Mg, Y, As, Sb, and REM is 0.0005
0.05%,
A steel sheet for hot forming having excellent impact characteristics and delayed fracture characteristics after hot forming, characterized by comprising balance Fe and inevitable impurities (including incidental impurities).
Ｃ ：０．１〜０．５５％、
Ｓｉ：１．０％以下、
Ｍｎ：０．２〜３％、
Ａｌ：０．００５〜０．１％、
Ｓ ：０．０２％以下、
Ｐ ：０．０３％以下、
Ｃｒ：０．０ｌ〜１％、
Ｂ：０．０００２〜０．００５％、
Ｃ，Ｎ，Ｔｉ量が３．９９×（Ｃ−０．１）≧Ｔｉ−３．４２×Ｎ≧０．００１を満 足し、
さらに、
Ｓｎを必須とし、Ｎｉ（ゼロを含む），Ｃｕ（ゼロを含む）の１種または２種を含 み、Ｓｎ，Ｎｉ，Ｃｕの合計が０．００５〜２％、
Ｃａ，Ｍｇ，Ｙ，Ａｓ，Ｓｂ，ＲＥＭの１種または２種以上の合計が０．０００５〜
０．０５％、
残部Ｆｅ及び不可避的不純物（付随的不純物を含む）からなることを特徴とする熱間成形加工後の衝撃特性・遅れ破壊特性に優れた熱間成形加工用鋼板。 % By mass
C: 0.1 to 0.55%,
Si: 1.0% or less,
Mn: 0.2-3%,
Al: 0.005 to 0.1%,
S: 0.02% or less,
P: 0.03% or less,
Cr: 0.01 to 1%,
B: 0.0002 to 0.005%,
The amount of C, N, and Ti satisfies 3.99 × (C−0.1) ≧ Ti−3.42 × N ≧ 0.001,
further,
The Sn as essential, Ni (including zero), viewed contains one or two of Cu (including zero), Sn, Ni, total of Cu from 0.005 to 2%,
The total of one or more of Ca, Mg, Y, As, Sb, and REM is 0.0005
0.05%,
A steel sheet for hot forming having excellent impact characteristics and delayed fracture characteristics after hot forming, characterized by comprising balance Fe and inevitable impurities (including incidental impurities).
Ｔｉ，Ｎｂ，Ｚｒ，Ｍｏ，Ｖの１種または２種以上の合計が０．００５％以上、かつ、Ｃ−１２×（Ｔｉ／４８＋Ｎｂ／９３＋Ｚｒ／９１＋Ｍｏ／９６＋Ｖ／５１）≧０．１
を満足するように含有することを特徴とする請求項１又は２に記載の熱間成形加工後の衝撃特性・遅れ破壊特性に優れた熱間成形加工用鋼板。 As ancillary components, in mass%,
The total of one or more of Ti, Nb, Zr, Mo, V is 0.005% or more, and C-12 × (Ti / 48 + Nb / 93 + Zr / 91 + Mo / 96 + V / 51) ≧ 0.1
The steel sheet for hot forming according to claim 1 or 2, having excellent impact characteristics and delayed fracture characteristics after hot forming.
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