JPH05125485A - High-tension galvannealed steel sheet having excellent plating adhesion and production thereof - Google Patents

High-tension galvannealed steel sheet having excellent plating adhesion and production thereof

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Publication number
JPH05125485A
JPH05125485A JP31349691A JP31349691A JPH05125485A JP H05125485 A JPH05125485 A JP H05125485A JP 31349691 A JP31349691 A JP 31349691A JP 31349691 A JP31349691 A JP 31349691A JP H05125485 A JPH05125485 A JP H05125485A
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JP
Japan
Prior art keywords
less
steel sheet
plating
hot
strength
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Granted
Application number
JP31349691A
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Japanese (ja)
Other versions
JP2953638B2 (en
Inventor
Hidenori Shirasawa
白沢秀則
Fukuteru Tanaka
田中福輝
Takahiro Kashima
鹿島高弘
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Kobe Steel Ltd
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Kobe Steel Ltd
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Abstract

PURPOSE:To provide the high-tension galvannealed steel sheet having excellent plating adhesion. CONSTITUTION:The steel sheet contains 0.01 to 0.3% C, 1.5 to 3.0% Mn, <=0.15% Si, <=0.1% P, and 0.01 to 0.1% Al, satisfies a relation Mn/Si>=3.0, contains, if necessary, one or >=2 kinds of <=1.0% Mo, <=0.01% B, <=0.1% Ti, <=0.1% Nb, <=0.1% Zr, <=1.0% Cr, <=1.0% Cu, <=1.0% Ni, <=0.1% V, and <=0.1% W, and consists of the balance Fe and unavoidable impurities. This steel sheet is produced by passing a plating bath at 400 to 460 deg.C bath temp. at the time of subjecting the steel consisting of the above-mentioned chemical components to hot rolling or cold rolling after the hot rolling, then passing the steel through a galvanizing line. The steel sheet is suitable for an ultra-high strength material, such as steel sheet for bumper members and door guard bars of automobiles for which high workability is needed.

Description

【発明の詳細な説明】Detailed Description of the Invention

【0001】[0001]

【産業上の利用分野】本発明は、高加工性が必要な自動
車のバンバー部材やドアガードバー用鋼板のような超高
強度材に適するめっき密着性に優れた合金化高張力溶融
亜鉛めっき鋼板及びその製造方法に関するものである。
FIELD OF THE INVENTION The present invention relates to an alloyed high-strength hot-dip galvanized steel sheet excellent in plating adhesion suitable for ultra-high strength materials such as automobile bar bar members and steel sheets for door guard bars which require high workability. The present invention relates to a manufacturing method thereof.

【0002】[0002]

【従来の技術】近年、自動車の軽量化や安全性、耐食性
の要求が高まり、これまでより、更に高い強度を有した
亜鉛めっき鋼板が使用されつつある。そして、この鋼板
の高強度化は加工性を劣化させるため、様々な加工性劣
化の防止策が試みられている。例えば、特公昭62−4
0405号などは、強度と加工性をフェライト・マルテ
ンサイト二相組織によって得ようとするものである。
2. Description of the Related Art In recent years, demands for weight reduction, safety and corrosion resistance of automobiles have increased, and galvanized steel sheets having higher strength than ever have been used. Since increasing the strength of this steel plate deteriorates workability, various measures for preventing workability deterioration have been attempted. For example, Japanese Patent Publication No. 62-4
No. 0405 and the like are intended to obtain strength and workability by a ferrite / martensite two-phase structure.

【0003】一方、溶融亜鉛めっき高張力鋼板において
は、高強度化に伴う様々な加工性の改善が検討されてい
るが、高延性高張力鋼板を得るために添加されるSi、
Pなどは、合金化特性を劣化させ、Γ相と言われる耐パ
ウダリング特性を劣化させる硬質相を生成させるため、
亜鉛めっきと鋼板素地との密着性や合金化特性の劣化が
問題であった。
On the other hand, in hot-dip galvanized high-strength steel sheets, various workability improvements have been studied in association with higher strength. Si added in order to obtain high-ductility high-strength steel sheets,
P or the like deteriorates alloying characteristics and generates a hard phase called Γ phase, which deteriorates powdering resistance characteristics.
Adhesion between galvanizing and steel sheet base and deterioration of alloying characteristics have been problems.

【0004】[0004]

【発明が解決しようとする課題】上述のように、合金化
溶融亜鉛めっき鋼板においては、場合によって亜鉛めっ
きと鋼板素地との密着性や合金化特性に問題が生じ、合
金化溶融亜鉛めっき鋼板の製造において、強度や加工特
性は良好であつても、めっきはぐり(パウダリング)や合
金化むらを生じていた。特に、高強度化に伴って元素を
添加する場合、Siなどの悪影響が大きかった。
As described above, in the alloyed hot-dip galvanized steel sheet, a problem may occur in the adhesion between the galvanization and the steel sheet substrate and the alloying characteristics in some cases. In the production, even though the strength and processing characteristics were good, galling (powdering) and uneven alloying occurred. In particular, when elements are added as the strength increases, adverse effects such as Si are large.

【0005】本発明は、上記従来技術の問題点を解決
し、めっき特性を改善すると共に高張力を有する合金化
溶融亜鉛めっき鋼板を提供し、またその製造方法を提供
することを目的とするものである。
An object of the present invention is to solve the above-mentioned problems of the prior art, to provide an alloyed hot-dip galvanized steel sheet having high tensile strength and improved plating characteristics, and to provide a method for producing the same. Is.

【0006】[0006]

【課題を解決するための手段】本発明者は、前記課題を
解決するため、鋼組成並びに製造条件について鋭意研究
を重ねた結果、合金化高張力溶融亜鉛めっき鋼板の成分
組成、特に低Si化と共にMn/Si比を規制し、かつ、
めっき浴温度を合わせて適正化することにより可能であ
ることを見い出し、ここに本発明を完成したものであ
る。
In order to solve the above-mentioned problems, the present inventor has conducted earnest studies on the steel composition and manufacturing conditions, and as a result, the composition of the alloyed high-strength hot-dip galvanized steel sheet, especially the reduction of Si. Regulates the Mn / Si ratio with
The inventors have found that this is possible by adjusting the temperature of the plating bath appropriately and completed the present invention.

【0007】すなわち、本発明は、C:0.01〜0.3
%、Mn:1.5〜3.0%、Si:0.5%以下、P≦0.1
%、Al:0.01〜0.1%を含み、かつ、Mn/Si≧
3.0の関係を満たし、必要に応じて更にMo:1.0%以
下、B:0.01%以下、Ti:0.1%以下、Nb:0.1%
以下、Zr:0.1%以下、Cr:1.0%以下、Cu:1.0
%以下、Ni:1.0%以下、V:0.1%以下、W:0.1
%以下のうちの1種又は2種以上を含有し、残部がFe
及び不可避的不純物よりなることを特徴とするめっき密
着性に優れた合金化高張力溶融亜鉛めっき鋼板を要旨と
するものである。
That is, the present invention uses C: 0.01 to 0.3.
%, Mn: 1.5 to 3.0%, Si: 0.5% or less, P ≦ 0.1
%, Al: 0.01 to 0.1%, and Mn / Si ≧
Satisfies the relationship of 3.0, and if necessary, Mo: 1.0% or less, B: 0.01% or less, Ti: 0.1% or less, Nb: 0.1%.
Below, Zr: 0.1% or less, Cr: 1.0% or less, Cu: 1.0
% Or less, Ni: 1.0% or less, V: 0.1% or less, W: 0.1
% Or less of 1 or 2 or more and the balance is Fe
And an alloyed high-strength hot-dip galvanized steel sheet excellent in plating adhesion, characterized by comprising unavoidable impurities.

【0008】また、その製造方法は、上記成分組成の鋼
を、熱延後又は熱延後冷延を施して溶融亜鉛めっきライ
ンを通す際に、めっき浴温度を400〜460℃にて通
板することを特徴とするものである。
Further, the manufacturing method is such that, when the steel having the above-described composition is hot-rolled or hot-rolled and then cold-rolled and passed through a hot dip galvanizing line, the plating bath temperature is 400 to 460 ° C. It is characterized by doing.

【0009】以下に本発明を更に詳細に説明する。The present invention will be described in more detail below.

【0010】[0010]

【作用】[Action]

【0011】まず、本発明における鋼の化学成分の限定
理由について説明する。
First, the reasons for limiting the chemical composition of steel in the present invention will be explained.

【0012】C:Cは鋼の強度に大きく作用し、第二相
変態生成物の量や形態を変えることができ、局部伸びや
フランジ加工特性に影響する元素である。このため、合
金化高張力溶融亜鉛めっき鋼板を得るために最も重要な
元素である。しかし、めっき特性にはあまり影響せず、
0.01%の少量添加から超高強度鋼を得るために必要
な0.3%添加量まで、めっき密着性や合金化速度を劣
化させることはない(図1参照)。また、Cは0.3%を
超えて添加すると溶接特性を劣化させるので好ましくな
い。よって、C量は0.01〜0.3%の範囲とする。
C: C is an element that has a large effect on the strength of steel, can change the amount and form of the second phase transformation product, and affects local elongation and flanging characteristics. Therefore, it is the most important element for obtaining an alloyed high-strength hot-dip galvanized steel sheet. However, it does not significantly affect the plating characteristics,
From the small addition amount of 0.01% to the addition amount of 0.3% necessary for obtaining the ultra high strength steel, the plating adhesion and the alloying rate are not deteriorated (see FIG. 1). Further, if C is added in an amount exceeding 0.3%, the welding characteristics are deteriorated, which is not preferable. Therefore, the amount of C is set to the range of 0.01 to 0.3%.

【0013】Mn:Mnはフェライトやオーステナイト中
の固溶C量を変化させ、γ相を安定化させる元素であ
り、冷却途中に生成する第二相変態生成物の特性を制御
するのに有効である。このため、高張力鋼板の様々な特
性を得るためには最低1.5%の添加量が必要である。
更に、この元素は合金化速度を速め、めっき密着性に良
好な効果をもたらす(図2参照)。この元素の添加量は、
めっき特性を劣化させる後述のSi量との関係において
Mn/Si≧3.0を満たす量にて添加することにより、
めっき密着性を向上させることができる(図6参照)。但
し、3.0%を超えて添加すると、亜鉛めっき中のFe濃
度を過度に高くし、逆に亜鉛めっきの防錆性を劣化させ
たり、Γ相の生成を促進する。よって、Mn量は1.5〜
3.0%の範囲とする。
Mn: Mn is an element that stabilizes the γ phase by changing the amount of solid solution C in ferrite or austenite, and is effective in controlling the characteristics of the second phase transformation product formed during cooling. is there. Therefore, in order to obtain various properties of the high-strength steel sheet, a minimum addition amount of 1.5% is necessary.
Furthermore, this element accelerates the alloying rate and brings about a good effect on the plating adhesion (see FIG. 2). The amount of this element added is
By adding in an amount that satisfies Mn / Si ≧ 3.0 in relation to the amount of Si described below that deteriorates the plating characteristics,
The plating adhesion can be improved (see FIG. 6). However, if added in excess of 3.0%, the Fe concentration in the galvanization becomes excessively high, and on the contrary, the rust preventive property of the galvanization is deteriorated and the generation of the Γ phase is promoted. Therefore, the amount of Mn is 1.5-
The range is 3.0%.

【0014】Si:Siはフェライト中に固溶して強度を
上げる元素であり、固溶強化の効果はPに次いで大き
い。このため、強度を確保するには最も有効な元素の一
つである。しかし、多量に添加すると、表面に酸化皮膜
を生成すると共に、亜鉛めっきの合金化速度をも遅く
し、めっきむらや不めっきの原因となる。その上限は
0.5%である(図3参照)。0.5%以下で、上述のMn
量との関係においてMn/Si≧3.0を満たす量にて添
加すれば、めっき密着性や合金化速度を劣化させること
がない。
Si: Si is an element that forms a solid solution in ferrite to increase the strength, and the effect of solid solution strengthening is the second largest after P. Therefore, it is one of the most effective elements for securing strength. However, when added in a large amount, an oxide film is formed on the surface and the alloying rate of zinc plating is also slowed, which causes uneven plating and non-plating. The upper limit is 0.5% (see FIG. 3). Below 0.5%, the above Mn
When added in an amount satisfying Mn / Si ≧ 3.0 in relation to the amount, the plating adhesion and alloying rate are not deteriorated.

【0015】P:Pは、Siと同様にフェライト中に固
溶し強度を上げる元素であり、固溶強化能の最も大きな
元素である。しかし、多量に添加すると、Siと同様に
めっきむらや不めっきを生じる場合がある。但し、Mn
量が1.5%以上であれば、0.1%まで添加しても、め
っき特性に対する劣化は生じない。よって、P量は0.
1%以下とする。
P: P is an element which, like Si, forms a solid solution in ferrite to increase strength and has the largest solid solution strengthening ability. However, if added in a large amount, uneven plating or non-plating may occur as in Si. However, Mn
If the amount is 1.5% or more, even if it is added up to 0.1%, the plating characteristics are not deteriorated. Therefore, the amount of P is 0.
1% or less.

【0016】Al:Alは脱酸剤として用いられ、通常
0.01%以上添加される。しかし、0.1%より多く添
加すると鋼中に介在物が生成し、延性を劣化させるた
め、Al量は0.01〜0.1%の範囲とする。
Al: Al is used as a deoxidizing agent and is usually added in an amount of 0.01% or more. However, if more than 0.1% is added, inclusions are formed in the steel and the ductility is deteriorated, so the Al content is made 0.01 to 0.1%.

【0017】上記成分のほか、本発明においては、必要
に応じて、以下の元素の1種又は2種以上を適量にて添
加することができ、めっき特性を向上させることができ
る。
In addition to the above components, in the present invention, one or more of the following elements can be added in appropriate amounts, if necessary, to improve the plating characteristics.

【0018】Mo、B:Mo、Bは鋼中の粒界に微量偏析
し、鋼中の粒界からの亜鉛めっきの浸入を防ぎ、溶融亜
鉛めっきによる割れや加工性劣化を防止する。特に、M
nの添加はこれらの元素の固溶限を変化させて偏析を促
進し、主に鋼表面に出た粒界部分を核にして生成するΓ
相の生成を防止する。添加する場合、Mo量が1.0%以
下、B量が0.01%以下であれば上記効果が得られ
る。
Mo, B: Mo and B are segregated in a small amount at grain boundaries in the steel, prevent zinc plating from penetrating from the grain boundaries in the steel, and prevent cracking and workability deterioration due to hot dip galvanization. In particular, M
The addition of n changes the solid solubility limit of these elements and promotes segregation, and is mainly formed by the grain boundary portion appearing on the steel surface as a nucleus.
Prevent the formation of phases. When added, if the Mo content is 1.0% or less and the B content is 0.01% or less, the above effect is obtained.

【0019】Ti、Nb、Zr:Ti、Nb、ZrはC量がお
よそ80ppm以上の場合、少なからず亜鉛めっき特性を
良好にする効果がある。Mn添加鋼にこれらの元素を添
加した場合にはMnによる亜鉛めっき密着性向上に加え
て、これらの元素の固溶限の拡大や拡散の増加により合
金化速度が向上する。しかし、Mn量が微量である場合
や、これらの元素を過度に添加すると、炭化物を生成し
フェライト粒界中のC濃度が下がるため、粒界からの亜
鉛めっき浸入やΓ相の生成によって、めっき特性を劣化
させる。よって、Ti、Nb、Zr量はそれぞれ0.1%以
下とする。
Ti, Nb, Zr: Ti, Nb, Zr have a considerable effect of improving the galvanizing characteristics when the amount of C is about 80 ppm or more. When these elements are added to Mn-added steel, in addition to the improvement of zinc plating adhesion by Mn, the alloying rate is improved by expanding the solid solution limit and diffusion of these elements. However, when the amount of Mn is very small or when these elements are excessively added, carbides are generated and the C concentration in the ferrite grain boundary is lowered, so that zinc plating infiltration from the grain boundary or generation of Γ phase causes plating. Deteriorate the characteristics. Therefore, the amounts of Ti, Nb, and Zr are each set to 0.1% or less.

【0020】Cr、Cu、Ni、V、W:Cr、Cu、Ni、
V、Wは、Mnと複合添加することにより、Γ相の生成
を抑え、めっきの密着性を上げる効果がある。また、こ
れらは耐食性を向上させる元素でもあるため、防錆性向
上に対して有効な元素である。そのためには、Cr、C
u、Ni量はそれぞれ1.0%以下、V、W量はそれぞれ
0.1%以下でよい。
Cr, Cu, Ni, V, W: Cr, Cu, Ni,
When V and W are added in combination with Mn, they have the effect of suppressing the formation of the Γ phase and increasing the adhesion of the plating. Further, since these are also elements that improve corrosion resistance, they are effective elements for improving rust resistance. For that purpose, Cr, C
The u and Ni amounts may be 1.0% or less, and the V and W amounts may be 0.1% or less.

【0021】次に、本発明の製造条件について説明す
る。
Next, the manufacturing conditions of the present invention will be described.

【0022】上記化学成分を有する鋼板は、熱延し、又
は熱延後冷延し、溶融亜鉛めっきラインにて製造される
が、めっき浴温が高い場合には浴中にて急速な合金化反
応を起こし、鋼板界面にΓ相を生じ易い。このため、め
っきを低温にて付着させ、昇温後、合金化することが好
ましい。しかし、400℃未満では亜鉛が完全に溶融し
ないことや、場合によってはめっき付着時に付着むらを
生じ合金化むらの原因となるため、溶融亜鉛めっきの浴
の温度を400〜460℃に限定する。なお、昇温速度
は特に制限されないが、およそ100℃/s以下が望ま
しい。他の合金化溶融亜鉛めっき条件は特に制限される
ものではない。
The steel sheet having the above chemical composition is hot-rolled, or hot-rolled and then cold-rolled, and is manufactured in a hot dip galvanizing line. However, when the temperature of the plating bath is high, rapid alloying is performed in the bath. It is easy to cause a reaction and generate a Γ phase at the steel sheet interface. For this reason, it is preferable to deposit the plating at a low temperature and then alloy it after raising the temperature. However, if the temperature is lower than 400 ° C, zinc is not completely melted, and in some cases, uneven adhesion occurs during plating adhesion, which causes uneven alloying. Therefore, the temperature of the hot dip galvanizing bath is limited to 400 to 460 ° C. The heating rate is not particularly limited, but is preferably about 100 ° C./s or less. Other galvannealing conditions are not particularly limited.

【0023】かくして得られる合金化高張力溶融亜鉛め
っき鋼板は、めっきはぐりや合金むらがない。しかも、
鋼板組織がベイナイトとフェライト又はベイナイトとフ
ェライトとマルテンサイトからなり、高強度で加工性も
良好である。
The alloyed high-strength hot-dip galvanized steel sheet thus obtained is free from galling and uneven alloy. Moreover,
The steel sheet structure is composed of bainite and ferrite or bainite, ferrite and martensite, and has high strength and good workability.

【0024】次に本発明の実施例を示す。Next, examples of the present invention will be described.

【0025】[0025]

【実施例】【Example】

【表1】 に示す化学成分を有する鋼板を用い、2.0mmの板厚に
冷間圧延した後、亜鉛めっき実験装置を用いて、焼鈍
後、亜鉛めっきを420℃にて施し、合金化処理を55
0℃にて行った。めっきは両面に片面で60mg/mm2
付着させた。
[Table 1] After cold rolling to a thickness of 2.0 mm using a steel sheet having the chemical composition shown in Table 1, after annealing using a galvanizing experimental device, galvanizing is performed at 420 ° C. and alloying treatment is performed to 55
Performed at 0 ° C. The plating applied 60 mg / mm 2 on one side to both sides.

【0026】耐パウダリング特性は、60秒の合金化処
理を行った鋼板を90°曲げた後、曲げ部分にテープを
貼り、テープに付着しためっき量によりを評価した。ま
た、合金化速度は、合金化時間を30〜90秒の範囲で
変化させ、めっき層に溶け込んだ鉄濃度により評価し
た。この結果は
The powdering resistance was evaluated by bending the steel sheet subjected to the alloying treatment for 60 seconds at 90 °, applying a tape to the bent portion, and measuring the amount of plating adhered to the tape. The alloying speed was evaluated by changing the alloying time within the range of 30 to 90 seconds and the concentration of iron dissolved in the plating layer. This result is

【表2】 に示す。[Table 2] Shown in.

【0027】表2において、鋼No.1〜No.4はC濃度
による影響を示し、No.5〜No.10はMn/Si比の影
響を示している。またNo.11〜No.21は他の添加元
素の影響を示している。表2より明らかなように、本発
明範囲の化学成分を有し、本発明範囲内の製造条件(め
っき浴温度420℃)で得られた本発明例は、いずれも
優れためっき密着性を示しており、また強度及び伸びと
も良好である。図4、図5、図6はMn/Si比の合金化
速度に及ぼす影響を整理したものである。
In Table 2, steel No. 1 to No. 4 show the effect of the C concentration, and No. 5 to No. 10 show the effect of the Mn / Si ratio. Further, No. 11 to No. 21 show the influence of other additive elements. As is clear from Table 2, the present invention examples having the chemical components within the scope of the present invention and obtained under the production conditions within the scope of the present invention (plating bath temperature 420 ° C.) all show excellent plating adhesion. The strength and elongation are also good. FIG. 4, FIG. 5, and FIG. 6 summarize the effects of the Mn / Si ratio on the alloying rate.

【0028】鋼No.2、No.10、No.17について、
めっき浴温度を400〜470℃の範囲で変化させた場
合の結果を
For steel No. 2, No. 10 and No. 17,
The results when the plating bath temperature was changed in the range of 400 to 470 ° C

【表3】 [Table 3] ,

【表4】 [Table 4] ,

【表5】 にそれぞれ示す。板厚2mm、めっき目付け量は両面に片
面で60mg/mm2である。各表より、めっき浴温度とし
ては420〜460℃が適正であることがわかる。
[Table 5] Are shown respectively. The plate thickness is 2 mm, and the coating weight is 60 mg / mm 2 on both sides. From each table, it is understood that the appropriate plating bath temperature is 420 to 460 ° C.

【0029】[0029]

【表6】 に、添加元素によるΓ相の発生状況の違いを示す。な
お、Γ相の発生状況の違いをより明確にするため、めっ
き付着温度(500℃)、合金化温度(600℃)を高く
し、合金化時間(3分)も長く設定し、図7に示す基準に
て1(優)→5(劣)のように判定した。その結果、同表に
示すように、Siが多い(No.7)と不めっきが多いが、
本発明範囲内の添加元素の場合は、Γ相の発生を防止し
得ることがわかる。
[Table 6] Figure 2 shows the difference in the generation state of the Γ phase due to the added elements. In order to clarify the difference in the generation state of the Γ phase, the plating adhesion temperature (500 ° C) and the alloying temperature (600 ° C) were set high, and the alloying time (3 minutes) was set long. Based on the criteria shown, it was judged as 1 (excellent) → 5 (poor). As a result, as shown in the table, when there is much Si (No. 7), there is much unplating,
It is understood that the addition element within the range of the present invention can prevent the generation of the Γ phase.

【0030】[0030]

【発明の効果】以上詳述したように、本発明によれば、
めっき密着性に優れると共に高張力を有する合金化溶融
亜鉛めっき鋼板を提供することができる。
As described in detail above, according to the present invention,
It is possible to provide a galvannealed steel sheet having excellent plating adhesion and high tension.

【図面の簡単な説明】[Brief description of drawings]

【図1】Cの合金化速度に及ぼす影響を示す図であり、
製造条件は板厚1.2mm、めつき浴温度450℃であ
る。
FIG. 1 is a diagram showing the effect of C on the alloying rate,
The manufacturing conditions are a plate thickness of 1.2 mm and a plating bath temperature of 450 ° C.

【図2】Mnの合金化速度に及ぼす影響を示す図であ
り、製造条件は板厚1.2mm、めつき浴温度450℃で
ある。
FIG. 2 is a diagram showing the effect of Mn on the alloying rate, and the manufacturing conditions are a plate thickness of 1.2 mm and a plating bath temperature of 450 ° C.

【図3】Siの合金化速度に及ぼす影響を示す図であ
り、製造条件は板厚1.2mm、めつき浴温度450℃で
ある。
FIG. 3 is a diagram showing the influence of Si on the alloying rate, and the production conditions are a plate thickness of 1.2 mm and a plating bath temperature of 450 ° C.

【図4】Mn/Si比の合金化速度に及ぼす影響を示す図
である。
FIG. 4 is a diagram showing the effect of the Mn / Si ratio on the alloying rate.

【図5】Mn/Si比及び添加元素(Mo、Ti、Cr)の合
金化速度に及ぼす影響を示す図である。
FIG. 5 is a diagram showing the effects of the Mn / Si ratio and the additive elements (Mo, Ti, Cr) on the alloying rate.

【図6】Mn/Si比の合金化速度に及ぼす影響を示す図
である。
FIG. 6 is a diagram showing the effect of the Mn / Si ratio on the alloying rate.

【図7】Γ相の発生状況の判定基準を説明する図で、
(a)はΓ相なしの場合(ランク1)、(b)はΓ相が局
部発生した場合(ランク3)、(c)はΓ相が1.0μm以
上連続して発生した場合(ランク5)である。
FIG. 7 is a diagram illustrating a criterion for determining a Γ-phase occurrence state,
(A) is the case without the Γ phase (rank 1), (b) is the case where the Γ phase is locally generated (rank 3), and (c) is the case where the Γ phase is continuously generated at 1.0 μm or more (rank 5). ).

───────────────────────────────────────────────────── フロントページの続き (51)Int.Cl.5 識別記号 庁内整理番号 FI 技術表示箇所 C23C 2/06 2/40 ─────────────────────────────────────────────────── ─── Continuation of the front page (51) Int.Cl. 5 Identification code Internal reference number FI technical display location C23C 2/06 2/40

Claims (5)

【特許請求の範囲】[Claims] 【請求項1】 重量%で(以下、同じ)、C:0.01〜
0.3%、Mn:1.5〜3.0%、Si:0.5%以下、P≦
0.1%、Al:0.01〜0.1%を含み、かつ、Mn/S
i≧3.0の関係を満たし、残部がFe及び不可避的不純
物よりなることを特徴とするめっき密着性に優れた合金
化高張力溶融亜鉛めっき鋼板。
1. By weight% (hereinafter the same), C: 0.01-
0.3%, Mn: 1.5 to 3.0%, Si: 0.5% or less, P ≦
0.1%, Al: 0.01 to 0.1%, and Mn / S
An alloyed high-strength hot-dip galvanized steel sheet having excellent plating adhesion, which satisfies the relation of i ≧ 3.0 and the balance is Fe and inevitable impurities.
【請求項2】 前記鋼が、更に、Mo:1.0%以下、B:
0.01%以下、Ti:0.1%以下、Nb:0.1%以下、
Zr:0.1%以下、Cr:1.0%以下、Cu:1.0%以
下、Ni:1.0%以下、V:0.1%以下、W:0.1%以
下のうちの1種又は2種以上を含有している請求項1に
記載の合金化高張力溶融亜鉛めっき鋼板。
2. The steel further comprises Mo: 1.0% or less and B:
0.01% or less, Ti: 0.1% or less, Nb: 0.1% or less,
Zr: less than 0.1%, Cr: less than 1.0%, Cu: less than 1.0%, Ni: less than 1.0%, V: less than 0.1%, W: less than 0.1% The alloyed high-strength hot-dip galvanized steel sheet according to claim 1, which contains one or more types.
【請求項3】 鋼板組織がベイナイトとフェライト又は
ベイナイトとフェライトとマルテンサイトからなる請求
項1又は2に記載の合金化高張力溶融亜鉛めっき鋼板。
3. The alloyed high-strength hot-dip galvanized steel sheet according to claim 1, wherein the steel sheet structure comprises bainite and ferrite or bainite, ferrite and martensite.
【請求項4】 C:0.01〜0.3%、Mn:1.5〜3.
0%、Si:0.5%以下、P≦0.1%、Al:0.01〜
0.1%を含み、かつ、Mn/Si≧3.0の関係を満た
し、残部がFe及び不可避的不純物よりなる鋼を、熱延
後又は熱延後冷延を施して溶融亜鉛めっきラインを通す
際に、めっき浴温度を400〜460℃にて通板するこ
とを特徴とするめっき密着性に優れた合金化高張力溶融
亜鉛めっき鋼板の製造方法。
4. C: 0.01 to 0.3%, Mn: 1.5 to 3.
0%, Si: 0.5% or less, P ≦ 0.1%, Al: 0.01 to
Steel containing 0.1% and satisfying the relationship of Mn / Si ≧ 3.0 and the balance Fe and unavoidable impurities is hot-rolled or cold-rolled after hot-rolling to form a hot dip galvanizing line. A method for producing an alloyed high-strength hot-dip galvanized steel sheet having excellent plating adhesion, which comprises passing a plating bath at a temperature of 400 to 460 ° C. when passing.
【請求項5】 前記鋼が、更に、Mo:1.0%以下、B:
0.01%以下、Ti:0.1%以下、Nb:0.1%以下、
Zr:0.1%以下、Cr:1.0%以下、Cu:1.0%以
下、Ni:1.0%以下、V:0.1%以下、W:0.1%以
下のうちの1種又は2種以上を含有している請求項4に
記載の方法。
5. The steel further comprises Mo: 1.0% or less and B:
0.01% or less, Ti: 0.1% or less, Nb: 0.1% or less,
Zr: less than 0.1%, Cr: less than 1.0%, Cu: less than 1.0%, Ni: less than 1.0%, V: less than 0.1%, W: less than 0.1% The method according to claim 4, which contains one or more kinds.
JP31349691A 1991-11-01 1991-11-01 Alloyed high-strength hot-dip galvanized steel sheet with excellent plating adhesion and manufacturing method thereof Expired - Lifetime JP2953638B2 (en)

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Application Number Priority Date Filing Date Title
JP31349691A JP2953638B2 (en) 1991-11-01 1991-11-01 Alloyed high-strength hot-dip galvanized steel sheet with excellent plating adhesion and manufacturing method thereof

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JPH05125485A true JPH05125485A (en) 1993-05-21
JP2953638B2 JP2953638B2 (en) 1999-09-27

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US6316127B1 (en) 1999-04-27 2001-11-13 Kobe Steel, Ltd. Galvanized steel sheet superior in ductility and process for production thereof
CN100392135C (en) * 2005-06-30 2008-06-04 宝山钢铁股份有限公司 Ultra-high strength strip steel and its production process
JP2013177681A (en) * 2012-02-08 2013-09-09 Nippon Steel & Sumitomo Metal Corp Steel plate for molten zinc bath equipment excellent in resistance to molten zinc corrosion and resistance to zinc-induced cracking and method for producing the same
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Cited By (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US6316127B1 (en) 1999-04-27 2001-11-13 Kobe Steel, Ltd. Galvanized steel sheet superior in ductility and process for production thereof
FR2794133A1 (en) * 1999-05-28 2000-12-01 Kobe Steel Ltd Hot dip galvanized steel sheet for car structural parts production has ferrite and martensite microstructure and contains manganese, chromium, molybdenum and aluminum
CN100392135C (en) * 2005-06-30 2008-06-04 宝山钢铁股份有限公司 Ultra-high strength strip steel and its production process
EP2762580A4 (en) * 2011-09-29 2015-06-03 Jfe Steel Corp Hot-dip galvanized steel sheet and method for producing same
JP2013177681A (en) * 2012-02-08 2013-09-09 Nippon Steel & Sumitomo Metal Corp Steel plate for molten zinc bath equipment excellent in resistance to molten zinc corrosion and resistance to zinc-induced cracking and method for producing the same
JP2013177682A (en) * 2012-02-08 2013-09-09 Nippon Steel & Sumitomo Metal Corp Steel plate for molten zinc bath equipment excellent in resistance to molten zinc corrosion and resistance to zinc-induced cracking and method for producing the same
JP2017122280A (en) * 2012-02-08 2017-07-13 新日鐵住金株式会社 Molten zinc bath installation
JP2017133106A (en) * 2012-02-08 2017-08-03 新日鐵住金株式会社 Molten zinc bath facility

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