JPH03274251A - Galvannealed steel sheet excellent in press formability - Google Patents
Galvannealed steel sheet excellent in press formabilityInfo
- Publication number
- JPH03274251A JPH03274251A JP7393790A JP7393790A JPH03274251A JP H03274251 A JPH03274251 A JP H03274251A JP 7393790 A JP7393790 A JP 7393790A JP 7393790 A JP7393790 A JP 7393790A JP H03274251 A JPH03274251 A JP H03274251A
- Authority
- JP
- Japan
- Prior art keywords
- layer
- phase
- steel sheet
- plating
- galvannealed
- 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.)
- Pending
Links
- 229910000831 Steel Inorganic materials 0.000 title abstract description 16
- 239000010959 steel Substances 0.000 title abstract description 15
- 238000007747 plating Methods 0.000 claims abstract description 51
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 13
- 239000000956 alloy Substances 0.000 claims abstract description 13
- 229910052742 iron Inorganic materials 0.000 claims abstract description 9
- 229910052759 nickel Inorganic materials 0.000 claims abstract description 6
- 238000002441 X-ray diffraction Methods 0.000 claims abstract description 5
- 229910001335 Galvanized steel Inorganic materials 0.000 claims description 17
- 239000008397 galvanized steel Substances 0.000 claims description 17
- 239000000203 mixture Substances 0.000 claims description 4
- 238000000227 grinding Methods 0.000 abstract description 13
- 238000000576 coating method Methods 0.000 abstract description 11
- 239000011248 coating agent Substances 0.000 abstract description 9
- 229910007567 Zn-Ni Inorganic materials 0.000 abstract description 7
- 229910007614 Zn—Ni Inorganic materials 0.000 abstract description 7
- 230000001105 regulatory effect Effects 0.000 abstract 4
- 229910000859 α-Fe Inorganic materials 0.000 abstract 2
- 238000005244 galvannealing Methods 0.000 abstract 1
- 239000010410 layer Substances 0.000 description 33
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 20
- 238000000034 method Methods 0.000 description 9
- 238000005275 alloying Methods 0.000 description 7
- 238000005260 corrosion Methods 0.000 description 7
- 230000007797 corrosion Effects 0.000 description 7
- 230000000694 effects Effects 0.000 description 7
- 238000012360 testing method Methods 0.000 description 6
- 239000011247 coating layer Substances 0.000 description 5
- 230000007423 decrease Effects 0.000 description 4
- 239000002184 metal Substances 0.000 description 4
- 229910052751 metal Inorganic materials 0.000 description 4
- 229910000990 Ni alloy Inorganic materials 0.000 description 3
- 239000011324 bead Substances 0.000 description 3
- 238000005452 bending Methods 0.000 description 3
- 230000015572 biosynthetic process Effects 0.000 description 3
- 238000005246 galvanizing Methods 0.000 description 3
- 238000010438 heat treatment Methods 0.000 description 3
- 239000000463 material Substances 0.000 description 3
- 239000011701 zinc Substances 0.000 description 3
- 229910001297 Zn alloy Inorganic materials 0.000 description 2
- 238000007792 addition Methods 0.000 description 2
- 230000002411 adverse Effects 0.000 description 2
- 230000000052 comparative effect Effects 0.000 description 2
- 238000009792 diffusion process Methods 0.000 description 2
- 238000009713 electroplating Methods 0.000 description 2
- 238000004519 manufacturing process Methods 0.000 description 2
- 229910052698 phosphorus Inorganic materials 0.000 description 2
- 239000000843 powder Substances 0.000 description 2
- 238000003825 pressing Methods 0.000 description 2
- 229910052725 zinc Inorganic materials 0.000 description 2
- 241000894006 Bacteria Species 0.000 description 1
- 229910052684 Cerium Inorganic materials 0.000 description 1
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 1
- 101000993059 Homo sapiens Hereditary hemochromatosis protein Proteins 0.000 description 1
- 229910052770 Uranium Inorganic materials 0.000 description 1
- HCHKCACWOHOZIP-UHFFFAOYSA-N Zinc Chemical compound [Zn] HCHKCACWOHOZIP-UHFFFAOYSA-N 0.000 description 1
- 238000009825 accumulation Methods 0.000 description 1
- 229910000905 alloy phase Inorganic materials 0.000 description 1
- 229910052782 aluminium Inorganic materials 0.000 description 1
- 239000004566 building material Substances 0.000 description 1
- 229910052793 cadmium Inorganic materials 0.000 description 1
- 229910052804 chromium Inorganic materials 0.000 description 1
- 238000004140 cleaning Methods 0.000 description 1
- 238000001816 cooling Methods 0.000 description 1
- 229910052802 copper Inorganic materials 0.000 description 1
- 239000010949 copper Substances 0.000 description 1
- 230000008021 deposition Effects 0.000 description 1
- 238000005530 etching Methods 0.000 description 1
- 238000011156 evaluation Methods 0.000 description 1
- 238000007654 immersion Methods 0.000 description 1
- 229910052738 indium Inorganic materials 0.000 description 1
- KFZAUHNPPZCSCR-UHFFFAOYSA-N iron zinc Chemical group [Fe].[Zn] KFZAUHNPPZCSCR-UHFFFAOYSA-N 0.000 description 1
- JEIPFZHSYJVQDO-UHFFFAOYSA-N iron(III) oxide Inorganic materials O=[Fe]O[Fe]=O JEIPFZHSYJVQDO-UHFFFAOYSA-N 0.000 description 1
- 229910052746 lanthanum Inorganic materials 0.000 description 1
- 239000002932 luster Substances 0.000 description 1
- 229910052748 manganese Inorganic materials 0.000 description 1
- 230000001590 oxidative effect Effects 0.000 description 1
- 239000003973 paint Substances 0.000 description 1
- 230000003449 preventive effect Effects 0.000 description 1
- 229910052717 sulfur Inorganic materials 0.000 description 1
- 229910052718 tin Inorganic materials 0.000 description 1
- 229910052719 titanium Inorganic materials 0.000 description 1
- 125000000391 vinyl group Chemical group [H]C([*])=C([H])[H] 0.000 description 1
- 229920002554 vinyl polymer Polymers 0.000 description 1
- 229910052726 zirconium Inorganic materials 0.000 description 1
Abstract
Description
【発明の詳細な説明】
（ａ業上の利用分野）
本発明は、プレス成形性に優れた合金化溶融亜鉛めっき
鋼板に関するものであり、特に合金化溶融亜鉛めっき鋼
板にとって重要な耐パウダリング性および耐フレーキン
グ性ともに満足するものである。Detailed Description of the Invention (Field of Application in Industry A) The present invention relates to an alloyed hot-dip galvanized steel sheet with excellent press formability, and in particular powdering resistance, which is important for an alloyed hot-dip galvanized steel sheet. and flaking resistance are both satisfactory.
合金化溶融亜鉛めっき鋼板は、溶融亜鉛めっき鋼板をめ
っき後加熱して素地鋼板の鉄をめっき層中に拡散させ、
鉄−亜鉛合金化するものであるが、亜鉛めっき鋼板に比
較して耐食性が優れているため、自動車、建材、家電製
品等の材料として広く使われている。Alloyed hot-dip galvanized steel sheet is produced by heating the hot-dip galvanized steel sheet after plating to diffuse the iron in the base steel sheet into the coating layer.
Although it is an iron-zinc alloy, it has superior corrosion resistance compared to galvanized steel sheets, so it is widely used as a material for automobiles, building materials, home appliances, etc.
（従来の技術）
近年、耐食性向上に対する要求から、厚目付の合金化熔
融亜鉛めっ＠鋼板が強く要望されている。しかし、合金
化溶融亜鉛めっき鋼板は熱拡散処理で製造するため、日
付量が厚くなるに従いめっき層中の鉄濃度勾配が大きく
なり、地鉄との界面にはＦｅ濃度の高く脆いｒ相が生威
しやすくなり、一方めっき層の表面近傍にはＦｅ濃度の
低いζ相や極端な場合は未合金となりη相が残存したり
する。(Prior Art) In recent years, due to the demand for improved corrosion resistance, there has been a strong demand for thicker alloyed galvanized @ steel sheets. However, since alloyed hot-dip galvanized steel sheets are manufactured by thermal diffusion treatment, the iron concentration gradient in the coating layer increases as the coating layer thickens, and a brittle r-phase with a high Fe concentration forms at the interface with the base iron. On the other hand, near the surface of the plating layer, a ζ phase with a low Fe concentration or, in extreme cases, an unalloyed η phase may remain.
ｒ相が厚いとプレス加工時にめっき層が剥離するパウダ
リングが生じやすくなるため、製品にめっき剥１１Ｉｌ
粉の押し疵等が発生し、歩留り低下や金型洗浄の頻度増
による能率低下等の弊害が出る。If the r-phase is thick, powdering, which causes the plating layer to peel off during press processing, is likely to occur, so the product is coated with
Powder dents and the like occur, resulting in adverse effects such as a decrease in yield and a decrease in efficiency due to an increase in the frequency of mold cleaning.
一方めっき層表面にζ相が厚く存在したり、η相が残存
すると、これらの相の摺動抵抗が大きいため、プレス加
工時に型かじりが生成しやすく、いわゆるフレーキング
となって金型ビード部等に堆積し、これまたプレス工程
の歩留り低下、能率低下をもたらす。On the other hand, if the ζ phase is thick or the η phase remains on the surface of the plating layer, the sliding resistance of these phases is large, so mold galling is likely to occur during press processing, resulting in so-called flaking and damage to the mold bead. This also causes a decrease in yield and efficiency in the pressing process.
このような、厚目付量（４５ｇ／ｙａ２以上の付着量）
の合金化溶融亜鉛めっき鋼板では、プレス工程での耐パ
ウダリング性、耐フレーキング性ともに満足することが
要求されている。Thick coverage amount (adhesion amount of 45g/ya2 or more)
The alloyed hot-dip galvanized steel sheet is required to satisfy both powdering resistance and flaking resistance during the pressing process.
また、低目付量では、δ、相を主体とするめっき層を形
成することにより、プレス成形性に優れた合金化溶融亜
鉛めっき鋼板が製造され実用に供されているものの、成
形性の向上は引き続き望まれている。In addition, at low coating weights, alloyed hot-dip galvanized steel sheets with excellent press formability have been manufactured and put into practical use by forming a plating layer mainly composed of δ phase, but the improvement in formability has not been achieved. continues to be desired.
（発明が解決しようとする課題）
従来の合金化溶融亜鉛めっき鋼板の製造方法は、溶融亜
鉛浴中に有効醐量（＾交％−Ｆｅ％）を例えば０．０９
〜０．１５％に添加調整した洛中に銅帯を通してめっき
をし、ガスワイピング等で目付量調整した後合金化炉に
通板し、めっき表面に金属光沢が消えるまで、即ち表面
まで合金化が完了する時点まで熱処理し、直ちに冷却し
て合金化程度を制御して製造していた（特開昭６１−２
２３１７４号公報）。かかるめっき層の組成は、Ｆｅ：
８〜１３％、Ａｌ ： ０．２５〜０．３５％、残部Ｚ
ｎからなるものである。(Problems to be Solved by the Invention) In the conventional manufacturing method of alloyed hot-dip galvanized steel sheets, an effective amount (^%-Fe%) of 0.09, for example, is added to the hot-dip zinc bath.
Copper strips are plated by passing them through a Raku medium whose addition has been adjusted to ~0.15%, and after adjusting the basis weight by gas wiping, etc., the strips are passed through an alloying furnace until the metallic luster disappears on the plating surface, that is, alloying is carried out to the surface. Manufactured by heat-treating until completion and immediately cooling to control the degree of alloying (Japanese Patent Laid-Open No. 61-2
23174). The composition of this plating layer is Fe:
8-13%, Al: 0.25-0.35%, balance Z
It consists of n.
しかるに目付量４５ ｇ／＋２以上の溶融亜鉛めっき鋼
板をかかる工程で合金化処理すると、地鉄界面に生成す
るｒ相の厚さが例えば１〜３μｍ程度となり、耐バウリ
ング性が十分ではない。However, when a hot-dip galvanized steel sheet with a basis weight of 45 g/+2 or more is alloyed in this process, the thickness of the r-phase formed at the interface between the steel base is, for example, about 1 to 3 μm, and the bowling resistance is not sufficient.
そこで浴中の有効Ａ１量を０．ｌＯ％以下程度に低減し
、洛中で形成されるＦｅ−Ａ１合金層を薄くしてＦｅ−
Ｚｎ合金相の生成を比較的容易にすることによって、よ
り低温の熱処理で合金化溶融亜鉛めっき鋼板を製造する
ことが出来る。Therefore, the effective amount of A1 in the bath was set to 0. By reducing the Fe-A1 alloy layer to less than 10% and thinning the Fe-A1 alloy layer formed in Raku, Fe-
By making the formation of the Zn alloy phase relatively easy, an alloyed hot-dip galvanized steel sheet can be produced by heat treatment at a lower temperature.
かかるめっき層の組成は、Ｆｅ：６〜１１％、Ａ皇：
０．０５〜０．２５％、残部ｚｎからなるものである。The composition of this plating layer is Fe: 6 to 11%, Fe:
It consists of 0.05 to 0.25% and the balance zn.
しかるに目付量４５ ｇ／ｍ”以上の場合には、ｒ相の
厚さを１μ嘗以下とする条件はあるものの、めっき層表
面にη相、ζ相が残存しやすく、耐フレーキング性が十
分ではない。However, when the basis weight is 45 g/m" or more, although there is a condition that the thickness of the r phase is 1 μm or less, the η phase and ζ phase tend to remain on the surface of the plating layer, and the flaking resistance is insufficient. isn't it.
このような欠点を解決するため、例えばめっき層の下層
（地鉄との境界）で生成する「相の生成を極力抑え、上
層部はη相、δ１相、ζ相からなるめっき層とし、また
溶融合金層上に鉄めっきを施すことが開示されている（
特開昭６０−２２８６１３２号公報）が、未だ満足すべ
き結果は得られていないのが現状である。In order to solve these drawbacks, for example, the formation of "phases" generated in the lower layer of the plating layer (at the boundary with the base steel) is suppressed as much as possible, and the upper layer is made of a plating layer consisting of η phase, δ1 phase, and ζ phase, and It is disclosed that iron plating is applied on the molten alloy layer (
However, the current situation is that satisfactory results have not yet been obtained.
（課題を解決するための手段）
そこで本発明者らは鋭意検討した結果、パウダリング、
ブレーキングともに満足する合金化溶融亜鉛めっき鋼板
を見いだした。(Means for Solving the Problems) Therefore, as a result of intensive study, the present inventors found that powdering,
We have found an alloyed hot-dip galvanized steel sheet that satisfies both braking performance.
上記問題点を解決するための本発明は、Ｆｅ６〜１３ｗ
ｔ％、残部Ｚｎからなる組成であって、地鉄−めっき界
面のｒ相が１．０μ■以下、めっき層のＸ線回折のメイ
ンピークがζ相であり、目付量２０〜ｌｏｏｇ／ｍ２の
合金化溶融亜鉛めっき層の上に、Ｎｉ５〜３０ｗｔ％、
残部７．ｎからなる合金めっきを０．？−５，０ｇ／ｍ
’被覆せしめためっき層を片面、または両面に有する耐
パウダリング性および耐フレーキング性ともに満足する
プレス成形性に優れた合金化溶融亜鉛めっき鋼板である
。The present invention for solving the above problems is based on Fe6-13w
t%, the balance being Zn, the r phase at the base metal-plating interface is less than 1.0μ■, the main peak of the X-ray diffraction of the plating layer is the ζ phase, and the basis weight is 20 to 100g/m2. On the alloyed hot-dip galvanized layer, 5 to 30 wt% Ni,
Remainder 7. alloy plating consisting of 0. ? -5,0g/m
This is an alloyed hot-dip galvanized steel sheet that has a coating layer on one or both sides and has excellent press formability and satisfies both powdering resistance and flaking resistance.
（作 用〉
ζ相は摺動抵抗が大きいためフレーキング性に劣るもの
の、伸び性がありパウダリングは生じにくい。また、曲
げ加工のみの場合には下層部で発生する亀裂の伝播を防
止する効果がある。このζ相の長所を活かし、短所であ
る摺動抵抗を上層の硬質のＺｎ−Ｎｉ合金めっきの潤滑
性により克服することにより、耐パウダリング性、耐フ
レーキング性ともに満足させたことが本発明の特徴であ
る。また、めっき層をＦｅ％の低いζ相主体とすること
により、バクダリング発生の大きな原因であるｒ相の生
成を抑制すること、裸耐食性に優れたＺｎ−Ｎｉ合金め
っきの存在により耐食性が向上することも大きな特徴で
ある。なお、本発明は厚目付に限らず付着量２０〜１０
０ｇ／ｍ”と広い付着量範囲で合金化溶融亜鉛めっき鋼
板のプレス成形性を向上させるものである。(Function) Although the ζ phase has high sliding resistance and is inferior in flaking properties, it is stretchable and powdering is less likely to occur.In addition, when only bending is performed, it prevents the propagation of cracks that occur in the lower layer. It is effective. By taking advantage of the advantages of this ζ phase and overcoming the disadvantage of sliding resistance with the lubricity of the hard Zn-Ni alloy plating on the upper layer, both powdering resistance and flaking resistance are satisfied. This is a feature of the present invention.Also, by making the plating layer mainly composed of ζ phase with low Fe%, the formation of r phase, which is a major cause of bacterium, can be suppressed, and Zn-Ni, which has excellent bare corrosion resistance, can be suppressed. Another major feature is that corrosion resistance is improved by the presence of alloy plating.The present invention is applicable not only to thick coatings but also to coatings with a coating weight of 20 to 10
It improves the press formability of alloyed hot-dip galvanized steel sheets over a wide coating weight range of 0 g/m''.
本発明の下地めっき鋼板は、例えばＡ工；０．００３〜
０．１３％の溶融亜鉛めっき浴でめっきを施し、次いで
加熱処理するに際し、板温：５２０〜４７０℃で１５秒
以内の加熱で、浴中醐量が少なくなる程低温側で熱処理
を施すことにより確実にζ相主体に製造できる。ζ相が
主体であることの確認は、電解剥離法、断面エツチング
法があるが、条件により得られる結果が変化するため、
好ましくはない。本発明でいうζ相主体とは、比較的容
易でめっき層構造を把握できるＸ線回折のメインピーク
とする。The base plated steel sheet of the present invention is, for example, A grade: 0.003~
When plating is applied in a 0.13% hot-dip galvanizing bath and then heat-treated, heat the plate at a temperature of 520 to 470°C within 15 seconds, and heat-treat at a lower temperature as the amount in the bath decreases. Therefore, it is possible to reliably manufacture the product mainly in the ζ phase. There are electrolytic stripping methods and cross-sectional etching methods to confirm that the ζ phase is the main component, but the results obtained vary depending on the conditions.
Not preferable. In the present invention, the term ζ-phase mainly refers to the main peak of X-ray diffraction, which is relatively easy to understand and allows the structure of the plating layer to be determined.
次いで、各構成要素の限定範囲について説明する。Next, the limited range of each component will be explained.
Ｆｅ外； Ｆｅ６％未満ではめっき層表面にη相が残存しやすい。Outside Fe; If Fe is less than 6%, the η phase tends to remain on the surface of the plating layer.
Ｆｅ１３％を超えるとγ相が１μｍを超えやすいので好
ましくない。If Fe exceeds 13%, the γ phase tends to exceed 1 μm, which is not preferable.
１層：
γ相は１μｍ以下とすることが、耐パウダリング性を向
上させるため好ましい。１μｍを超えると特に目付量４
５ ｇ／ｍ’以上では耐パウダリング性を劣化し、プレ
ス成形性に際し弊害が出る。1 layer: It is preferable that the γ phase has a thickness of 1 μm or less in order to improve powdering resistance. Especially when it exceeds 1 μm, the basis weight is 4.
If it exceeds 5 g/m', powdering resistance deteriorates and press formability is adversely affected.
ｚｎ−Ｎｉ合金めっき；
Ｚｎ−Ｎｉ合金めっきの存在によって金型へのめっき金
属の凝着を抑制でき、耐フレーキング性を改善できる。Zn-Ni alloy plating: The presence of Zn-Ni alloy plating can suppress adhesion of the plating metal to the mold and improve flaking resistance.
Ｚｎ−Ｎｉ合金めっきの付着量は０．２〜５．０ｇ／ｍ
２が好ましい。０．２ｇ／１１１’未満では下層めっき
層を完全に被覆することは困難で、下Ｎｎｎ郡部らの金
型凝着が起こる場合があり、好ましくない。５．０ｇ／
ｎ’を超えるとＺｎ−Ｎｉ合金めっきが硬質であるため
、このＺｎ−Ｎｉ合金めっきによるプレス成形性劣化が
生じるので好ましくない。なお、Ｚｎ−Ｎｉ合金めっき
のＮ４％は耐食性が最も良好なγ相が出現する５〜３０
ｗｔ％とし、好ましくはγ相が主体となる８〜１５ｗｔ
％がよい。また、めっき中にはＺｎ、 Ｎｉ以外に耐食
性、塗装密着性向上等の目的でＣｏ、 Ｆｅ、 Ｐ等の
元素が含まれていてもプレス成形性には同様な効果が発
揮できるので、これらの元素の添加も本発明の範嘲に入
る。Ｚｎ−Ｎｉ合金めっきのめっき法は特に限定しない
が、通常行なわれる電気めっき法が容易である。The coating weight of Zn-Ni alloy plating is 0.2 to 5.0 g/m
2 is preferred. If it is less than 0.2 g/111', it is difficult to completely cover the lower plating layer, and adhesion of the lower plated layer to the mold may occur, which is not preferable. 5.0g/
If n' is exceeded, the Zn--Ni alloy plating is hard, and the press formability of the Zn--Ni alloy plating deteriorates, which is not preferable. In addition, N4% of Zn-Ni alloy plating is 5 to 30, where the γ phase with the best corrosion resistance appears.
wt%, preferably 8 to 15 wt mainly composed of γ phase
% is good. In addition, even if the plating contains elements such as Co, Fe, and P in addition to Zn and Ni for the purpose of improving corrosion resistance and paint adhesion, they can have the same effect on press formability. Additions of elements also fall within the scope of the invention. The plating method for Zn--Ni alloy plating is not particularly limited, but a commonly used electroplating method is easy.
めっき付着量：
本発明の合金化溶融亜鉛めっき層の厚さは、目付量とし
て２０〜１００ｇ／ｍ２が適用できる範囲である。２０
ｇ／ｖａ２未満では耐食性に問題がある。１００ｇ／
ω２を超えると、γ相を１μｍ以下でめっきすることは
実際上困難である。Plating coverage: The thickness of the alloyed hot-dip galvanizing layer of the present invention is within a range of 20 to 100 g/m2 as a basis weight. 20
If it is less than g/va2, there is a problem in corrosion resistance. 100g/
When ω2 is exceeded, it is practically difficult to plate the γ phase with a thickness of 1 μm or less.
合金化溶融亜鉛めっき層の組成としてＦｅのみを規定し
たが、他の成分、例えばＡｆｆｉ、 Ｐｂ、 Ｃｄ。Although only Fe is specified as the composition of the alloyed hot-dip galvanized layer, other components such as Affi, Pb, and Cd may be included.
Ｓｎ、 Ｉｎ、 Ｌｌ、 Ｓｂ、 八ｓ、
Ｂｉ、 Ｍｇ、 Ｌａ、 Ｃｅ、 Ｔｉ。Sn, In, Ll, Sb, 8s,
Bi, Mg, La, Ce, Ti.
Ｚｒ、 Ｎｉ、 Ｃｏ、 Ｃｒ、 Ｍｎ、 Ｐ、 Ｓ、
Ｏ等が少量添加されたり、不可避的に混入しても、本
質的には本発明の効果は変わらないものである。特にＡ
Ｕに関しては、現行のプロセスではめっきおよび合金化
の制御のために、めっき浴中に０．１％前後添加されて
おり、めっき層にも必然的に混入している。ζ相主体の
めつき層となる限り、本発明に対しこのようなへ２量の
肥響はない。また、Ａ！Ｑの存在しない電気亜鉛めっき
材の熱拡散合金化材でもζ相主体の合金相になるのであ
れば、本質的に本発明の効果は発揮できる。Zr, Ni, Co, Cr, Mn, P, S,
Even if a small amount of O or the like is added or unavoidably mixed, the effects of the present invention essentially remain the same. Especially A
Regarding U, in the current process, approximately 0.1% of U is added to the plating bath to control plating and alloying, and it is inevitably mixed in the plating layer. As long as the plated layer is mainly composed of the ζ phase, the present invention does not have such a negative effect on the amount of ζ. Also, A! The effect of the present invention can be essentially achieved even in a thermal diffusion alloyed electrogalvanized material in which Q is not present, as long as the alloy phase is mainly composed of the ζ phase.
本発明のめっき層は、両面２０〜１００８７ｍ”の目付
量の防錆鋼板の場合には、両面に通用することが好まし
いが、片面２０〜１００８／ｍ’でかつ他面が付着量の
少ない差厚めつき鋼板の場合には、厚目付面のみに適用
することもできる。片面めっき鋼板の場合には勿論めっ
き面のみに適用するものである。The plating layer of the present invention is preferably applicable to both sides in the case of a rust preventive steel plate with a coating weight of 20 to 10087 m'' on both sides, but it is preferable that the coating layer has a coating weight of 20 to 1008/m' on one side and a small coating weight on the other side. In the case of a thickly plated steel plate, it can be applied only to the thickened surface.In the case of a single-sided plated steel plate, it can of course be applied only to the plated surface.
（実 施 例）
次に本発明の実施例を比較例とともに挙げる。めっき用
素材としてはＣＣ−＾１−に鋼（０，８ｔ Ｘ １００
０ｗ Ｘ ｃ ）を使用し、無酸化炉型の連続溶融亜鉛
めっきラインにおいてめっき直後に合金化処理炉により
、連続的に加熱合金化処理した。(Example) Next, examples of the present invention will be described together with comparative examples. The material for plating is CC-^1- steel (0.8t x 100
Immediately after plating in a continuous hot-dip galvanizing line of a non-oxidizing furnace type, heat alloying treatment was carried out using an alloying treatment furnace.
なおめっき浴中有効Ａ１は０．１０ｗｔ％で、めっき層
中Ｆｅ濃度は合金化炉の加熱条件を適宜に選定して製造
した。The effective A1 in the plating bath was 0.10 wt%, and the Fe concentration in the plating layer was manufactured by appropriately selecting the heating conditions of the alloying furnace.
通板速度は４０〜７０ｆｉＩ／分とし、浸漬時間は２〜
５秒の間の条件でめっきを行なった。また、電気めっき
ラインにて２ｎ−旧合金めっき（１２％Ｎｉ）をＯ，１
ｇ／ｍ”〜７ ｇ／ｍ’施しｋ。The plate threading speed is 40 to 70 fiI/min, and the immersion time is 2 to 70 fiI/min.
Plating was performed for 5 seconds. In addition, 2n-old alloy plating (12%Ni) was applied to O, 1 in the electroplating line.
g/m” to 7 g/m’alms k.
次にめっき層の加工性試験方法について述べる。Next, the method for testing the workability of the plating layer will be described.
■ 耐パウダリング性試験
加工前に曲げ加工部にビニールテープを貼り、テープ面
を内側とする曲げ加工（２Ｔ曲げ）を行ない、再度間い
てテープをはがし、めっき層がテープに付着して黒変し
た部分の程度で判定した。■ Powdering resistance test Before processing, apply vinyl tape to the bent part, perform bending with the tape side on the inside (2T bending), remove the tape again, and check that the plating layer adheres to the tape and turns black. Judgment was made based on the extent of the damage.
（良）◎−〇−△−×（劣）
（◎、○は実用上問題無し〉
■ 耐フレーキング性試験
角ビード付引張底形により評価した。ボンチーダイス間
を２．Ｏｋｇｆ／ｃａ＋” （プラグサイズ０．７Ｘ
７５ｘ ２８０ｍ１で試験片を押圧し、次いで試験片
を引張りなからビード部を通過させる。(Good) ◎-〇-△- Size 0.7X
Press the test piece with 75x280 ml and then pass the test piece through the bead without pulling.
２００枚の反復成形を行ない、鋼板またはビード部への
めっき層金属の堆積程度を相対評価した。200 sheets were repeatedly molded, and the degree of deposition of the plating layer metal on the steel plate or bead portion was relatively evaluated.
（良）◎−〇−△−×（劣）
（◎、Ｏは実用上問題無し）
■ 実プレス試験
普通乗用車のフェンダ一部品を実プレスで成形加工した
。３００枚の反復成形を行ない、鋼板またはプレス型へ
のめっき金属の付着堆積程度を相対評価した。評価は各
部位にテープを貼り付け、はがしてからテープに転着し
た金属粉の黒化度合いで判定した。(Good) ◎-〇-△-× (Poor) (◎, O means no problem in practical use) ■ Actual press test A part of the fender of an ordinary passenger car was formed using an actual press. 300 sheets were repeatedly molded, and the degree of adhesion and accumulation of the plated metal on the steel plate or press mold was evaluated relative to each other. The evaluation was based on the degree of blackening of the metal powder transferred to the tape after attaching tape to each area and removing it.
（良）◎−〇−△−×（劣）
（（０）、 Ｏは実用上問題無し）
上記それぞれの試験結果を比較例とともに第１表に示す
。(Good) ◎-〇-△-× (Poor) ((0), O indicates no problem in practical use) The above test results are shown in Table 1 along with comparative examples.
（発明の効果）
以上説明したごとく本発明のめっき鋼板は、パウダリン
グ性、フレーキング性ともに満足し、合金化溶融亜鉛め
っき鋼板の用途を拡大し、工業的に大きな効果を奏する
ものである。(Effects of the Invention) As explained above, the plated steel sheet of the present invention satisfies both powdering properties and flaking properties, expands the uses of alloyed hot-dip galvanized steel sheets, and has great industrial effects.
他４名4 others
Claims (1)
て、地鉄−めっき界面のΓ相が１．０μｍ以下、めっき
層のＸ線回折のメインピークがζ相であり、目付量２０
〜１００ｇ／ｍ＾２の合金化溶融亜鉛めっき層の上に、
Ｎｉ５〜３０ｗｔ％、残部Ｚｎからなる合金めっきを０
．２〜５．０ｇ／ｍ＾２被覆せしめためっき層を片面、
または両面に有することを特徴とするプレス成形性に優
れた合金化溶融亜鉛めっき鋼板。1 Composition consisting of 6 to 13 wt% Fe, balance Zn, the Γ phase at the base metal-plating interface is 1.0 μm or less, the main peak of the X-ray diffraction of the plating layer is the ζ phase, and the basis weight is 20
On top of ~100g/m^2 alloyed hot-dip galvanized layer,
Alloy plating consisting of 5 to 30 wt% Ni and the balance Zn
．． 2-5.0g/m^2 coated plating layer on one side,
Or an alloyed hot-dip galvanized steel sheet with excellent press formability, characterized by having a galvanized steel sheet on both sides.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP7393790A JPH03274251A (en) | 1990-03-23 | 1990-03-23 | Galvannealed steel sheet excellent in press formability |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP7393790A JPH03274251A (en) | 1990-03-23 | 1990-03-23 | Galvannealed steel sheet excellent in press formability |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH03274251A true JPH03274251A (en) | 1991-12-05 |
Family
ID=13532530
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP7393790A Pending JPH03274251A (en) | 1990-03-23 | 1990-03-23 | Galvannealed steel sheet excellent in press formability |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH03274251A (en) |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2011052268A1 (en) * | 2009-10-26 | 2011-05-05 | 新日本製鐵株式会社 | Alloyed hot-dip galvanized steel sheet having excellent formability and post-adhesion detachment resistance, and manufacturing method therefor |
| WO2011052269A1 (en) * | 2009-10-26 | 2011-05-05 | 新日本製鐵株式会社 | Alloyed hot-dip galvanized steel sheet and manufacturing method therefor |
| WO2022124812A1 (en) * | 2020-12-11 | 2022-06-16 | 주식회사 포스코 | High-strength galvannealed steel sheet having excellent powdering resistance and manufacturing method therefor |
-
1990
- 1990-03-23 JP JP7393790A patent/JPH03274251A/en active Pending
Cited By (9)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2011052268A1 (en) * | 2009-10-26 | 2011-05-05 | 新日本製鐵株式会社 | Alloyed hot-dip galvanized steel sheet having excellent formability and post-adhesion detachment resistance, and manufacturing method therefor |
| WO2011052269A1 (en) * | 2009-10-26 | 2011-05-05 | 新日本製鐵株式会社 | Alloyed hot-dip galvanized steel sheet and manufacturing method therefor |
| CN102575330A (en) * | 2009-10-26 | 2012-07-11 | 新日本制铁株式会社 | Alloyed hot-dip galvanized steel sheet and manufacturing method therefor |
| JP5146607B2 (en) * | 2009-10-26 | 2013-02-20 | 新日鐵住金株式会社 | Alloyed hot-dip galvanized steel sheet and manufacturing method thereof |
| JP5168417B2 (en) * | 2009-10-26 | 2013-03-21 | 新日鐵住金株式会社 | Alloyed hot-dip galvanized steel sheet excellent in formability and peel resistance after adhesion and method for producing the same |
| US9040168B2 (en) | 2009-10-26 | 2015-05-26 | Nippon Steel & Sumitomo Metal Corporation | Galvannealed steel sheet having excellent formability and exfoliation resistance after adhesion and production method thereof |
| US9133536B2 (en) | 2009-10-26 | 2015-09-15 | Nippon Steel & Sumitomo Metal Corporation | Galvannealed steel sheet and producing method thereof |
| US9903022B2 (en) | 2009-10-26 | 2018-02-27 | Nippon Steel 7 Sumitomo Metal Corporation | Production method of galvannealed steel sheet having excellent formability and exfoliation resistance after adhesion |
| WO2022124812A1 (en) * | 2020-12-11 | 2022-06-16 | 주식회사 포스코 | High-strength galvannealed steel sheet having excellent powdering resistance and manufacturing method therefor |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| JP2008214681A (en) | Galvannealed steel sheet superior in image clarity of coating and press formability, and manufacturing method therefor | |
| JPS5891162A (en) | Manufacture of galvanized steel plate | |
| JP3267178B2 (en) | Zn-Al alloy plated steel sheet with excellent workability | |
| JP4555499B2 (en) | Hot-dip Zn-Al-Mg-Si plated steel with excellent surface properties and method for producing the same | |
| JPH0581662B2 (en) | ||
| JP2783453B2 (en) | Hot-dip Zn-Mg-Al plated steel sheet and method for producing the same | |
| JP2841889B2 (en) | Manufacturing method of alloyed hot-dip galvanized steel sheet | |
| CN116685706B (en) | Plated steel material | |
| JPH03274251A (en) | Galvannealed steel sheet excellent in press formability | |
| JP4696364B2 (en) | Hot-dip galvanized steel sheet with excellent corrosion resistance and surface appearance | |
| JPH11140587A (en) | Galvannealed steel sheet excellent in plating adhesion | |
| JPH04360A (en) | Galvannealed steel sheet excellent in workability | |
| JPS648069B2 (en) | ||
| JP2002004017A (en) | HOT-DIP Zn-Al-Mg-Si PLATED STEEL MATERIAL EXCELLENT IN SURFACE CHARACTERISTIC AND ITS PRODUCTION METHOD | |
| JPH03274285A (en) | Galvannealed steel sheet excellent in press formability | |
| JPH03243755A (en) | Organic composite alloying hot dip galvanized steel sheet excellent in press formability | |
| JP2772697B2 (en) | Anti-corrosion steel sheet for automobiles with excellent low-temperature chipping resistance and perforation corrosion resistance | |
| JPH09202952A (en) | High workability galvanized steel sheet and its production | |
| JP2000169948A (en) | Hot dip galvannealed steel sheet and its production | |
| JP3766655B2 (en) | Method for producing high-Si high-strength galvannealed steel sheet with excellent plating adhesion and workability | |
| JPH04359A (en) | Galvannealed steel sheet excellent in corrosion resistance | |
| JPH07233458A (en) | Production of zn-al alloy plated steel | |
| JPH03274284A (en) | Galvannealed steel sheet excellent in press formability | |
| JP2724045B2 (en) | Method for producing chromium-containing steel sheet plated with hot-dip zinc or zinc alloy | |
| JPH04378A (en) | Alloyed molten zinc plates steel sheet having superior outside and inside corrosion resistance |