JPH02163356A - Production of alloyed hot dip galvanized steel sheet for working having superior powdering resistance - Google Patents
Production of alloyed hot dip galvanized steel sheet for working having superior powdering resistanceInfo
- Publication number
- JPH02163356A JPH02163356A JP31840388A JP31840388A JPH02163356A JP H02163356 A JPH02163356 A JP H02163356A JP 31840388 A JP31840388 A JP 31840388A JP 31840388 A JP31840388 A JP 31840388A JP H02163356 A JPH02163356 A JP H02163356A
- Authority
- JP
- Japan
- Prior art keywords
- less
- hot
- steel sheet
- dip galvanized
- powdering resistance
- 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
Links
- 238000000227 grinding Methods 0.000 title claims abstract description 29
- 229910001335 Galvanized steel Inorganic materials 0.000 title claims abstract description 18
- 239000008397 galvanized steel Substances 0.000 title claims abstract description 18
- 238000004519 manufacturing process Methods 0.000 title claims description 9
- 229910000831 Steel Inorganic materials 0.000 claims abstract description 23
- 239000010959 steel Substances 0.000 claims abstract description 23
- 238000005246 galvanizing Methods 0.000 claims abstract description 14
- 238000005275 alloying Methods 0.000 claims abstract description 8
- 238000000137 annealing Methods 0.000 claims abstract description 8
- 229910052757 nitrogen Inorganic materials 0.000 claims abstract description 8
- 238000001953 recrystallisation Methods 0.000 claims abstract description 8
- 238000005096 rolling process Methods 0.000 claims abstract description 8
- 239000012535 impurity Substances 0.000 claims abstract description 4
- 229910052698 phosphorus Inorganic materials 0.000 claims abstract description 4
- 229910052717 sulfur Inorganic materials 0.000 claims abstract description 4
- 230000009466 transformation Effects 0.000 claims abstract description 4
- 229910052760 oxygen Inorganic materials 0.000 claims abstract 4
- 238000012545 processing Methods 0.000 claims description 8
- 238000000034 method Methods 0.000 claims description 7
- 238000005098 hot rolling Methods 0.000 claims description 5
- 229910045601 alloy Inorganic materials 0.000 claims description 3
- 239000000956 alloy Substances 0.000 claims description 3
- 238000005097 cold rolling Methods 0.000 claims description 3
- 238000005452 bending Methods 0.000 abstract description 3
- 229910052799 carbon Inorganic materials 0.000 abstract description 3
- 230000001105 regulatory effect Effects 0.000 abstract description 2
- 229910052782 aluminium Inorganic materials 0.000 abstract 2
- 238000007747 plating Methods 0.000 description 5
- 239000000203 mixture Substances 0.000 description 4
- 229910001209 Low-carbon steel Inorganic materials 0.000 description 3
- 230000000694 effects Effects 0.000 description 3
- 239000000463 material Substances 0.000 description 3
- 238000007796 conventional method Methods 0.000 description 2
- 230000007797 corrosion Effects 0.000 description 2
- 238000005260 corrosion Methods 0.000 description 2
- 230000006866 deterioration Effects 0.000 description 2
- 238000011160 research Methods 0.000 description 2
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 1
- 229910000640 Fe alloy Inorganic materials 0.000 description 1
- HCHKCACWOHOZIP-UHFFFAOYSA-N Zinc Chemical compound [Zn] HCHKCACWOHOZIP-UHFFFAOYSA-N 0.000 description 1
- 229910000905 alloy phase Inorganic materials 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 239000003575 carbonaceous material Substances 0.000 description 1
- 230000000052 comparative effect Effects 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 230000005611 electricity Effects 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 238000011156 evaluation Methods 0.000 description 1
- 238000011835 investigation Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 150000004767 nitrides Chemical class 0.000 description 1
- 230000006911 nucleation Effects 0.000 description 1
- 238000010899 nucleation Methods 0.000 description 1
- 238000005204 segregation Methods 0.000 description 1
- 238000009864 tensile test Methods 0.000 description 1
- 238000010998 test method Methods 0.000 description 1
- 239000011701 zinc Substances 0.000 description 1
- 229910052725 zinc Inorganic materials 0.000 description 1
Landscapes
- Coating With Molten Metal (AREA)
Abstract
Description
【発明の詳細な説明】
（産業上の利用分野）
この発明は、曲げ加工、プレス成形加工、絞り成形加工
、深絞り加工および超深絞り加工などの用途に用いて好
適な加工用合金化溶融亜鉛めっき鋼板の製造方法に関し
、とくに加工時における耐パウダリング性の有利な改善
を図ったものである。DETAILED DESCRIPTION OF THE INVENTION (Field of Industrial Application) The present invention provides an alloyed melting material suitable for use in applications such as bending, press forming, drawing, deep drawing, and ultra-deep drawing. The present invention relates to a method for manufacturing galvanized steel sheets, and is particularly aimed at advantageously improving powdering resistance during processing.
（従来の技術）
合金化溶融亜鉛めっき鋼板は、その優れた耐食性とスポ
ット溶接性ゆえに、近年多量に使用されている。と（に
、その使用量の増加は、自動車の車体部品において顕著
である。(Prior Art) Alloyed hot-dip galvanized steel sheets have been widely used in recent years because of their excellent corrosion resistance and spot weldability. In addition, the increase in its usage is remarkable in automobile body parts.
ところでかような合金化溶融亜鉛めっき鋼板は、プレス
加工などの加工時に合金化溶融亜鉛めっき層が破壊し易
く、鋼板からはく離してパウダリングと呼ばれるトラブ
ルを引き起し易いという問題があった。However, such an alloyed hot-dip galvanized steel sheet has a problem in that the alloyed hot-dip galvanized layer is easily destroyed during processing such as press working, and easily peels off from the steel sheet, causing a problem called powdering.
とはいえ溶融亜鉛めっき法は電気亜鉛めっき法に比べる
と厚めつきがはるかに容易であり、従って鋼板使用製品
の耐食性向上という観点からは、合金化溶融亜鉛めっき
鋼板の耐パウダリング性を向上させることはきわめて重
要な技術である。However, the hot-dip galvanizing method is much easier to build up a thick layer than the electrogalvanizing method, and therefore, from the perspective of improving the corrosion resistance of products using steel sheets, it is possible to improve the powdering resistance of alloyed hot-dip galvanized steel sheets. This is an extremely important technology.
溶融亜鉛めっき鋼板に関する従来技術としては、次のよ
うなものがある。Conventional techniques related to hot-dip galvanized steel sheets include the following.
たとえば特開昭５８−１１０６５９号公報には、Ｔｉ、
Ｎｂ。For example, in Japanese Patent Application Laid-Open No. 58-110659, Ti,
Nb.
Ｂなどを単独または複合添加した極低炭素鋼を素材とす
る溶融亜鉛めっき鋼板が開示されているが、耐パウダリ
ング性に関する記述はない。A hot-dip galvanized steel sheet made of ultra-low carbon steel to which B or the like is added singly or in combination is disclosed, but there is no description regarding powdering resistance.
また特開昭５８−２５４３６号公報には、Ｔｉおよび■
を添加した極低炭素鋼を素材とする溶融亜鉛めっき鋼板
の製造例が開示されているが、やはり耐パウダリング性
に関する記述はない。Furthermore, in Japanese Patent Application Laid-Open No. 58-25436, Ti and ■
An example of manufacturing a hot-dip galvanized steel sheet using ultra-low carbon steel added with is disclosed, but there is no description regarding powdering resistance.
さらに特開昭６３−２４１１２２号公報には、Ｔｉを必
須とする極低炭素鋼を用いて焼付硬化性と超深絞り性を
向上させた溶融亜鉛めっき鋼板の製造方法が開示されて
いるが、同じく耐パウダリング性に関する記述はない。Furthermore, JP-A No. 63-241122 discloses a method for manufacturing a hot-dip galvanized steel sheet with improved bake hardenability and ultra-deep drawability using ultra-low carbon steel that essentially contains Ti. Similarly, there is no description regarding powdering resistance.
（発明が解決しようとする課題）
プレス成形等の加工性に優れるのはいうまでもなく、と
くに、加工時における耐パウダリング性に優れる鋼板を
得ることが、この発明の目的である。(Problems to be Solved by the Invention) It is an object of the present invention to obtain a steel plate that not only has excellent workability such as press forming, but also has particularly excellent powdering resistance during processing.
（課題を解決するための手段）
さて発明者らは、合金化溶融亜鉛めっき鋼板の耐パウダ
リング性の向上を図るべく鋭意研究を重ねた結果、とく
にＯ，ＡＩおよびＮの成分組成を適正範囲に規制するこ
とが、所期した目的の達成に関し、極めて有効であるこ
とを突き止め、この発明を完成させるに至ったのである
。(Means for Solving the Problems) As a result of intensive research aimed at improving the powdering resistance of alloyed hot-dip galvanized steel sheets, the inventors have found that the composition of O, AI and N in particular has been adjusted to an appropriate range. It was discovered that regulating the amount of electricity is extremely effective in achieving the intended purpose, and this led to the completion of this invention.
すなわちこの発明は、
Ｃ： ０．００２８ ｗｔχ （以下単に％と示す）以
下、Ｓｉ ： ０．２％以下、
Ｍｎ ： １．０％以下、
Ｐ ： ０．１５％以下、
Ｓ ： ０．０２００％以下、
０ ： ０．００４５％以下、
Ｎ ： ０．００３０％以下および
ＡＩ ： （２５×％Ｎ）〜０．１５％を含み、と
きにはさらに
Ｎｂ ： ０．００１〜０．０２５％およびＢ ：
０．０００２〜０．００２０％のうちから選んだ少な
くとも一種
を含有し、残部はＦｅおよび不可避的不純物からなるＮ
片を、６００℃以上の仕上げ温度で熱間圧延したのち、
圧下率＝６０％以上で冷間圧延し、引続き連続溶融亜鉛
めっきラインにてへ〇：ｌ変態点以下の温度で再結晶焼
鈍を施してから溶融亜鉛めっきを施し、しかるのち６５
０〜４２０℃の温度範囲で合金化処理を施すことからな
る耐パウダリング性に優れる加工用合金溶融亜鉛めっき
鋼板の製造方法である。That is, this invention has the following properties: C: 0.0028 wtχ (hereinafter simply referred to as %) or less, Si: 0.2% or less, Mn: 1.0% or less, P: 0.15% or less, S: 0.0200%. Below, 0: 0.0045% or less, N: 0.0030% or less, and AI: (25×%N) to 0.15%, and sometimes further Nb: 0.001 to 0.025% and B:
Contains at least one selected from 0.0002 to 0.0020%, with the remainder consisting of Fe and inevitable impurities.
After hot rolling the piece at a finishing temperature of 600°C or higher,
Cold rolled at a rolling reduction ratio of 60% or more, followed by continuous hot dip galvanizing line〇: Recrystallization annealed at a temperature below the transformation point, then hot dip galvanizing, then 65
This is a method for manufacturing a working alloy hot-dip galvanized steel sheet with excellent powdering resistance, which comprises performing an alloying treatment in a temperature range of 0 to 420°C.
（作 用）
合金化溶融亜鉛めっき鋼板の耐パウダリング性は、主に
加工用途に使われるこの種の鋼板においては極めて重要
な特性であるにも係わらず、従来、鋼成分の影’ｆｆに
関する研究は少ない。(Function) Although the powdering resistance of alloyed hot-dip galvanized steel sheets is an extremely important property for this type of steel sheet that is mainly used for processing purposes, it has traditionally been difficult to understand the effects of steel composition. There are few studies.
発明者らは、合金化溶融亜鉛めっき口板の耐パラダリン
グ性に及ぼす鋼成分の影響について研究を重ねた結果、
以下に述べる知見を得た。As a result of repeated research on the influence of steel components on the palladdering resistance of alloyed hot-dip galvanized mouth plates, the inventors found that
We obtained the findings described below.
第１図に、耐パウダリング性と鋼板中のｏｌおよびＡｌ
／Ｎ比との関係について調べた結果を示す。Figure 1 shows powdering resistance and OL and Al in steel sheets.
The results of an investigation regarding the relationship with /N ratio are shown.
なおＯ，ＡＩ、Ｎ以外の成分については表１に示すとお
りである。また耐パウダリング性は、密着曲げ変形を行
なった試片を曲げ戻したとき、内側部分だったところに
テープを貼り付けてはく離した亜鉛めっきを付着させ、
蛍光Ｘ線にて黒化度（ＣＰＳ）を測定することによって
評価するものとし、この試験法において黒化度が５００
ＣＰＳ以下であれば実用上パウダリング性に問題はない
といえる。Note that components other than O, AI, and N are as shown in Table 1. In addition, powdering resistance was determined by attaching tape to the inner part of the specimen and attaching the peeled zinc plating when the specimen was bent back after being subjected to close bending deformation.
The evaluation shall be made by measuring the degree of blackening (CPS) using fluorescent X-rays, and in this test method, the degree of blackening is 500.
If it is below CPS, it can be said that there is no problem in powdering property in practical terms.
同図より明らかなように、０量が０．００４５％以下で
かつＡｌ／Ｎ比が２５以上の場合に、実用上問題となら
ない優れた耐パウダリング性が得られた。As is clear from the figure, when the zero amount was 0.0045% or less and the Al/N ratio was 25 or more, excellent powdering resistance that did not cause any practical problems was obtained.
ここに上記の範囲の０量およびＡｌ／Ｎ比において耐パ
ウダリング性が向上した理由は、鋼板とめっき層の界面
においてＺｎ −Ｆｅ合金の核生成サイトとなり得る酸
化物もしくは窒化物の存在状態が変化し、不均一な合金
相の形成が抑制された結果と考えられる。The reason why the powdering resistance was improved in the above range of 0 amount and Al/N ratio is that the existence state of oxides or nitrides that can become nucleation sites of Zn-Fe alloy at the interface between the steel sheet and the plating layer is This is thought to be the result of suppressing the formation of a heterogeneous alloy phase.
なお第１図中に比較のために示したとおり、従来鋼板の
１つであるＴｉ添加鋼では、０量およびＡｌ／Ｎ比を所
定の範囲に調整しても耐パウダリング性は向上しなかっ
た。As shown for comparison in Figure 1, in Ti-added steel, which is one of the conventional steel sheets, the powdering resistance did not improve even if the amount of Ti and the Al/N ratio were adjusted within the specified range. Ta.
さらにＮｂおよび／またはＢを適正量添加した場合には
耐パウダリング性が一層向上することも併せて見いださ
れた。Furthermore, it has also been found that powdering resistance is further improved when an appropriate amount of Nb and/or B is added.
以下、この発明において素材の成分組成を前記の範囲に
限定した理由について述べる。The reason why the component composition of the material is limited to the above range in this invention will be described below.
Ｃ：Ｃは、良好な伸び、ｒ値を有する鋼板を得るために
は従来の低炭材より低い掻低炭素系でなければならない
。したがってＣは極力低減することが好ましいが、０．
００２８％以下で許容できる。とくに好ましい範囲は０
．００１５％以下である。C: In order to obtain a steel plate with good elongation and r-value, C must be a low-carbon type with a lower carbon content than conventional low-carbon materials. Therefore, it is preferable to reduce C as much as possible, but 0.
0.0028% or less is acceptable. A particularly preferable range is 0
．． 0015% or less.
Ｓｒ ： Ｓｉ は０．２％を超えて多量に含有される
とめっき密着性が著しく劣化するので０．２％以下とす
る。Sr: If Si is contained in a large amount exceeding 0.2%, the plating adhesion will deteriorate significantly, so the content is set to 0.2% or less.
Ｍｎ ： Ｍｎは過剰に添加すると鋼板の伸びおよび絞
り性が劣化するので、１．０％以下とする。Mn: If excessively added, Mn deteriorates the elongation and drawability of the steel sheet, so it should be kept at 1.0% or less.
ＦＤＰは０．１５％を超えて含有されると粒界への偏析
量が増し脆化するので０．１５％以下に制限した。If FDP is contained in an amount exceeding 0.15%, the amount of segregation at grain boundaries increases and embrittlement occurs, so it is limited to 0.15% or less.
ＳＯ３は０．０２００％を超えて多量に添加されると附
食性の急激な劣化を招くので０．０２００％以下に制限
する。とはいえあまりに低すぎると熱間圧延時における
脱スケール性が劣化し表面性状が悪化するので、０．０
０３５％以上とするのが好ましい。If SO3 is added in a large amount exceeding 0.0200%, it will cause rapid deterioration of the eating property, so it is limited to 0.0200% or less. However, if it is too low, the descaling property during hot rolling will deteriorate and the surface quality will deteriorate, so 0.0
It is preferable to set it to 0.035% or more.
０：０の範囲はこの発明においてとくに重要であり、０
量を０．００４５％以下まで抑制しないと良好な附パウ
ダリング性は得られない。従って０含有〒１よ０．００
４５％以下好ましくは０．００３５％以下とする必要が
ある。The range 0:0 is particularly important in this invention;
Good powdering properties cannot be obtained unless the amount is suppressed to 0.0045% or less. Therefore, 0 containing 〒1 0.00
It needs to be 45% or less, preferably 0.0035% or less.
ＮＵＮが多くなると材質が劣化するだけでなく、後述す
るように必要とするＡＩＮが過剰となり表面性状を劣化
させるので、０．００３０％以下とする。とくに好まし
い範囲は０．００２０％以下である。If NUN increases, not only will the material deteriorate, but as will be described later, the required AIN becomes excessive and deteriorates the surface quality, so it is set to 0.0030% or less. A particularly preferable range is 0.0020% or less.
Ａｔ ： Ａｌの範囲もこの発明においてとくに重要で
あり、Ｎｉとの関係においてＡＩ／Ｎが２５以上必要で
ある。というのはＡｌ／Ｎが２５未満では耐パウダリン
グ性が劣化するからである。なおとくに好ましいＡｌ／
Ｎ比は３０以上である。The range of At:Al is also particularly important in this invention, and AI/N is required to be 25 or more in relation to Ni. This is because if Al/N is less than 25, powdering resistance deteriorates. Particularly preferred Al/
The N ratio is 30 or more.
しかしながらあまりに多量の添加は、上述したとおり表
面性状の劣化を招くので、０．１５％以下とする必要が
ある。However, since adding too much leads to deterioration of the surface properties as described above, it is necessary to limit the amount to 0.15% or less.
以上述べたところのほか、この発明においては、耐パウ
ダリング性の向上を目的として、Ｎｂ ： ０．００１
〜０．０２５％、Ｂ ： ０．０００２〜０゜００２０
％の１種もしくは２種を添加することができる。In addition to what has been described above, in this invention, for the purpose of improving powdering resistance, Nb: 0.001
~0.025%, B: 0.0002~0°0020
% or two types can be added.
次にこの発明に従う製造法について説明する。Next, a manufacturing method according to the present invention will be explained.
先ず製鋼法については、常法に従って行えば良く、この
発明ではそれらの条件はと（に限定しない。熱間圧延に
おいては、仕上げ温度が６００℃に満たないと深絞り性
が劣化するので、６００℃以上とする。冷間圧延におい
ては少なくとも６０％の圧下率でないと十分な加工性が
得られない。ついで連続溶融亜鉛めっきラインに供する
。かかるめっきラインにおける焼鈍温度は、通常のごと
く再結晶温度以上であればよいが、望ましくは（１次再
結晶温度＋３０℃）以上で焼鈍するのがよい、また焼鈍
温度がＡｃ＝を超えると粗大な結晶粒となるのでＡｃ３
点以下の温度で焼鈍する必要がある。かような焼鈍後、
連続的に溶融亜鉛めっきを施し、さらに６００〜４２０
℃の温度範囲で合金化処理を施す。First, regarding the steel manufacturing method, it may be carried out according to a conventional method, and in this invention, those conditions are not limited to (. ℃ or higher.In cold rolling, sufficient workability cannot be obtained unless the rolling reduction is at least 60%.Next, it is subjected to a continuous hot-dip galvanizing line.The annealing temperature in such a galvanizing line is normally the recrystallization temperature. It is preferable to anneal at a temperature higher than (primary recrystallization temperature + 30°C), and if the annealing temperature exceeds Ac=, coarse crystal grains will result, so Ac3
It is necessary to anneal at a temperature below the point. After such annealing,
Continuously hot-dip galvanized and further coated with 600~420
Alloying treatment is carried out in the temperature range of °C.
なおめっき後に、板形状矯正などの目的で通常範囲（板
厚（＋１１０１）％程度）で調質圧延を行っても構わな
い。Note that after plating, temper rolling may be performed in a normal range (about (+1101)% of the plate thickness) for the purpose of straightening the plate shape or the like.
（実施例）
表２に示す種々の組成になる鋼スラブを、仕上げ温度＝
８６０〜９１０″Ｃで熱間圧延したのち、圧下率＝７２
〜７９％で冷間圧延して板厚：０．８ａｍの冷延板とし
た。ついで連続溶融亜鉛めっきラインにて８００〜８５
０ ℃の温度範囲で再結晶焼鈍を施してから、浴温：４
５０℃の溶融亜鉛めっき浴に浸漬することによって溶融
亜鉛めっき（めっき付着ｆｉ＝片側約４０ｇ／ｍ２）を
施し、引続き炉温５３０℃の合金化炉に導いて合金化処
理を施し、しかるのち０．８％の調質圧延を施した。(Example) Steel slabs with various compositions shown in Table 2 were prepared at a finishing temperature of
After hot rolling at 860-910″C, rolling reduction = 72
It was cold-rolled at ~79% to obtain a cold-rolled plate having a thickness of 0.8 am. Then 800~85 on a continuous hot dip galvanizing line.
After recrystallization annealing in the temperature range of 0 °C, bath temperature: 4
Hot-dip galvanizing (plating adhesion fi = about 40 g/m2 on one side) was performed by immersing the steel in a hot-dip galvanizing bath at 50°C, followed by an alloying process in an alloying furnace with a furnace temperature of 530°C. .8% temper rolling was performed.
かくして得られた合金化溶融亜鉛めっき鋼板の機械的緒
特性および耐パウダリング性について調べた結果を表３
に示す。Table 3 shows the results of investigating the mechanical properties and powdering resistance of the thus obtained alloyed hot-dip galvanized steel sheet.
Shown below.
なお機械的性質は、ＪＩＳ Ｎα５引張り試験片を用い
て求めた。また耐パウダリング性については前述したと
おりである。Note that the mechanical properties were determined using a JIS Nα5 tensile test piece. Further, the powdering resistance is as described above.
表３より明らかなように、この発明に従い得られた合金
化溶融亜鉛めっき鋼板はいずれも、Ｎα１０〜１６の比
較例およびＮｏ、 １７の従来例に比べて、格段に優れ
た耐パウダリング性を呈している。As is clear from Table 3, all the alloyed hot-dip galvanized steel sheets obtained according to the present invention have significantly better powdering resistance than the comparative examples with Nα10 to 16 and the conventional examples with No. 17. It is showing.
（発明の効果）
かくしてこの発明によれば、加工用鋼板としての機械的
緒特性に優れるのはいうまでもなく、従来鋼板に比較し
て格段に優れた耐パウダリング性を有する加工用合金化
溶融亜鉛めっき鋼板を得ることができる。(Effects of the Invention) Thus, according to the present invention, an alloy for processing has not only excellent mechanical properties as a steel plate for processing, but also has significantly superior powdering resistance compared to conventional steel plates. A hot-dip galvanized steel sheet can be obtained.
第１図は、耐パウダリング性に及ぼす鋼中０量およびＡ
ｌ／Ｎ比の影響を示したグラフである。Figure 1 shows the effect of 0 content in steel and A on powdering resistance.
It is a graph showing the influence of l/N ratio.
Claims (1)
片を、６００℃以上の仕上げ温度で熱間圧延したのち、
圧下率：６０％以上で冷間圧延し、引続き連続溶融亜鉛
めっきラインにてＡｃ＿３変態点以下の温度で再結晶焼
鈍を施してから溶融亜鉛めっきを施し、しかるのち６５
０〜４２０℃の温度範囲で合金化処理を施すことを特徴
とする耐パウダリング性に優れる加工用合金化溶融亜鉛
めっき鋼板の製造方法。 ２、Ｃ：０．００２８ｗｔ％以下、 Ｓｉ：０．２ｗｔ％以下、 Ｍｎ：１．０ｗｔ％以下、 Ｐ：０．１５ｗｔ％以下、 Ｓ：０．０２００ｗｔ％以下、 Ｏ：０．００４５ｗｔ％以下、 Ｎ：０．００３０ｗｔ％以下および Ａｌ：（２５×％Ｎ）〜０．１５ｗｔ％ を含み、かつ Ｎｂ：０．００１〜０．０２５ｗｔ％およびＢ：０．０
００２〜０．００２０ｗｔ％ のうちから選んだ少なくとも一種 を含有し、残部はＦｅおよび不可避的不純物からなる鋼
片を、６００℃以上の仕上げ温度で熱間圧延したのち、
圧下率：６０％以上で冷間圧延し、引続き連続溶融亜鉛
めっきラインにてＡｃ＿３変態点以下の温度で再結晶焼
鈍を施してから溶融亜鉛めっきを施し、しかるのち６５
０〜４２０℃の温度範囲で合金化処理を施すことを特徴
とする耐パウダリング性に優れる加工用合金溶融亜鉛め
っき鋼板の製造方法。[Claims] 1. C: 0.0028wt% or less, Si: 0.2wt% or less, Mn: 1.0wt% or less, P: 0.15wt% or less, S: 0.0200wt% or less, O: A steel piece containing 0.0045 wt% or less, N: 0.0030 wt% or less, and Al: (25×%N) to 0.15 wt%, with the balance consisting of Fe and unavoidable impurities, is heated to a finishing temperature of 600°C or higher. After hot rolling,
Cold rolling at a rolling reduction ratio of 60% or more, followed by recrystallization annealing at a temperature below the Ac_3 transformation point in a continuous hot-dip galvanizing line, followed by hot-dip galvanizing, then 65%
A method for producing an alloyed hot-dip galvanized steel sheet for processing, which has excellent powdering resistance, characterized by performing alloying treatment in a temperature range of 0 to 420°C. 2, C: 0.0028wt% or less, Si: 0.2wt% or less, Mn: 1.0wt% or less, P: 0.15wt% or less, S: 0.0200wt% or less, O: 0.0045wt% or less, Contains N: 0.0030 wt% or less and Al: (25 × % N) ~ 0.15 wt%, and Nb: 0.001 ~ 0.025 wt% and B: 0.0
After hot rolling a steel billet containing at least one selected from 0.002 to 0.0020 wt%, the remainder consisting of Fe and unavoidable impurities at a finishing temperature of 600°C or higher,
Cold rolling at a rolling reduction ratio of 60% or more, followed by recrystallization annealing at a temperature below the Ac_3 transformation point in a continuous hot-dip galvanizing line, followed by hot-dip galvanizing, then 65%
A method for producing an alloy hot-dip galvanized steel sheet for processing that has excellent powdering resistance, the method comprising performing alloying treatment in a temperature range of 0 to 420°C.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP63318403A JPH0627313B2 (en) | 1988-12-19 | 1988-12-19 | Method for producing alloyed hot-dip galvanized steel sheet having excellent powdering resistance |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP63318403A JPH0627313B2 (en) | 1988-12-19 | 1988-12-19 | Method for producing alloyed hot-dip galvanized steel sheet having excellent powdering resistance |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH02163356A true JPH02163356A (en) | 1990-06-22 |
| JPH0627313B2 JPH0627313B2 (en) | 1994-04-13 |
Family
ID=18098764
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP63318403A Expired - Fee Related JPH0627313B2 (en) | 1988-12-19 | 1988-12-19 | Method for producing alloyed hot-dip galvanized steel sheet having excellent powdering resistance |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH0627313B2 (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2010222676A (en) * | 2009-03-25 | 2010-10-07 | Sumitomo Metal Ind Ltd | Hot dip galvannealed steel sheet and method for producing the same |
Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5825436A (en) * | 1981-08-10 | 1983-02-15 | Kawasaki Steel Corp | Manufacture of deep drawing cold rolling steel plate having slow aging property and small anisotropy |
| JPS6156245A (en) * | 1984-08-24 | 1986-03-20 | Nippon Kokan Kk <Nkk> | Manufacture of molten galvanized steel sheet for deep drawing |
| JPS6160860A (en) * | 1984-09-03 | 1986-03-28 | Nippon Kokan Kk <Nkk> | Zinc plated steel sheet for deep drawing, superior in plating adhesion and its manufacture |
-
1988
- 1988-12-19 JP JP63318403A patent/JPH0627313B2/en not_active Expired - Fee Related
Patent Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5825436A (en) * | 1981-08-10 | 1983-02-15 | Kawasaki Steel Corp | Manufacture of deep drawing cold rolling steel plate having slow aging property and small anisotropy |
| JPS6156245A (en) * | 1984-08-24 | 1986-03-20 | Nippon Kokan Kk <Nkk> | Manufacture of molten galvanized steel sheet for deep drawing |
| JPS6160860A (en) * | 1984-09-03 | 1986-03-28 | Nippon Kokan Kk <Nkk> | Zinc plated steel sheet for deep drawing, superior in plating adhesion and its manufacture |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2010222676A (en) * | 2009-03-25 | 2010-10-07 | Sumitomo Metal Ind Ltd | Hot dip galvannealed steel sheet and method for producing the same |
Also Published As
| Publication number | Publication date |
|---|---|
| JPH0627313B2 (en) | 1994-04-13 |
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