JP3382697B2 - Manufacturing method of galvannealed steel sheet - Google Patents
Manufacturing method of galvannealed steel sheetInfo
- Publication number
- JP3382697B2 JP3382697B2 JP01047994A JP1047994A JP3382697B2 JP 3382697 B2 JP3382697 B2 JP 3382697B2 JP 01047994 A JP01047994 A JP 01047994A JP 1047994 A JP1047994 A JP 1047994A JP 3382697 B2 JP3382697 B2 JP 3382697B2
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- steel sheet
- temperature
- plating
- hot
- Prior art date
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Description
【発明の詳細な説明】
【０００１】
【産業上の利用分野】本発明は、自動車車体外板等に用
いられる合金化溶融亜鉛めっき鋼板の製造方法に関する
ものである。
【０００２】
【従来の技術】近年、自動車車体の防錆力強化が求めら
れ、向上策として亜鉛系の表面処理鋼板が指向されてい
る。その中で、特に溶融亜鉛めっき鋼板は経済的に優れ
ており、更に、加熱処理によりめっき層をFe−Zn合金
（合金化溶融亜鉛めっき鋼板）とすることにより溶接性
と塗装後の耐蝕性を改善することが出来る。
【０００３】自動車車体の外板に用いられる合金化溶融
亜鉛めっき（以下ＧＡと称する）鋼板は、意匠性を高め
る目的で高度のプレス加工が施されるため、求められる
材質として、延性と絞り性（ランクフォード値）はより
高いものになっている。これらの解決策としては、特開
平3-271354号公報、特開平1-184227号公報、特開平4-66
647 号公報等に示されているように、鋼材の材質面では
鋼中のＣ、Ｎ、Ｐ、Ｓ等の低減ならびにこれに伴う最適
な熱延、冷延プロセスが多数提案されている。
【０００４】一方、ＧＡ鋼板のめっき層に求められる特
性としては、加工時の鋼板の変形に追随できずに粉化し
て剥離するパウダリングが起こりにくいことが求められ
る。パウダリングが発生するとプレスダイスに溜まって
押し疵を発生させるとともにめっき本来の防食性を失わ
せるので問題になる。ＧＡ鋼板のめっき層は一般には低
Fe含有率から順にζ、δ1 、Γの３つのZn−Fe合金相か
らなるといわれ、パウダリングに付いてはΓ相が原因に
なるといわれている。
【０００５】ところで、前述のＣ、Ｎ、Ｐ、Ｓ等の低減
材に溶融亜鉛めっきを行いＧＡ鋼板を製造したところ、
延性、ｒ値の材質は満足するが、鋼板粒界での合金化を
過度に加速してしまい、Γ相形成量を増加させ、耐パウ
ダリング性を低下させることが明らかになった。
【０００６】
【発明が解決しようとする課題】本発明の目的は、鋼中
のＣ、Ｎ、Ｐ、Ｓを低減して高い鋼材材質を得、かつ美
麗な外観と優れた耐パウダリング性を有する合金化溶融
亜鉛めっき鋼板の製造方法提供することである。
【０００７】
【課題を解決するための手段】本発明の要旨とするとこ
ろは次の如くである。すなわち重量比で、
Ｃ：0.0015％以下、
Si：0.10％以下、
Mn：0.03〜0.30％、
Al：0.01〜0.10％、
Ｐ：0.01％以下、
Ｓ：0.005 ％以下、
Ｏ：0.005 ％以下、
Ｎ：0.005 ％以下、
Ti：0.010 ％以下、
Ｂ：0.001 ％以下
を含み、かつNbを0.03％以下で、Ｃ／12≦Nb／93≦Ｃ／
2 を満足する範囲で含み、残部実質的にFeからなる鋼板
をめっき素地鋼板として、連続式溶融亜鉛めっき装置で
合金化溶融亜鉛めっきを行うに際して、めっき浴のAl濃
度を重量比で0.12〜0.18％、Pb濃度を0.1 ％以下とし、
かつ、めっき浴温を 450〜 480℃とし、かつ、めっき浴
への鋼板浸入温度を 380℃〜( 浴温＋15℃) とし、か
つ、めっき浴Al濃度〔ＣAl（重量％）〕と浴温〔ＴＢ
（℃）〕と侵入板温〔ＴＳ（℃）〕が次式
ＴＢ／ＣAl＋ＴＳ≦4000
を満足させ、かつ、鋼板到達温度が 450〜 550℃の温度
範囲で合金化処理を行い、めっき層中のFe濃度を 7〜12
重量％とし、かつ、めっきの目付量を25〜75g/m2とする
ことを特徴とする合金化溶融亜鉛めっき鋼板の製造方法
である。
【０００８】
【作用】本発明者らは、合金化溶融亜鉛めっき鋼板のめ
っき相構成に及ぼす鋼中のＣ、Ｎ、Ｐ、Ｓ、Ti、Nb量、
めっき浴組成、合金化温度等を詳細に検討した結果、合
金化処理前の溶融亜鉛めっき条件が合金化後の溶融亜鉛
めっき鋼板のめっき特性に大きく作用することを明らか
にした。
【０００９】以下に本発明の目的である加工性と美麗な
外観、耐パウダリング性に優れる合金化溶融亜鉛めっき
鋼板を得るための製造条件について詳細に述べる。ま
ず、めっき素材となる鋼板の組成は、求められる材質と
経済性の点から、次のように決定される。
Ｃ：0.0015％以下
Ｃは鋼の強度を直接決定する元素であり、本発明の目的
である極めて高い加工性〔高い伸び（Ｅｌ）、ランクフ
ォード値（ｒ値）〕を得るには含有量は少ない程良く、
0.0015％以下とする。
【００１０】Ｎ：0.005 ％以下、Ｐ：0.01％以下、Ｓ：
0.005 ％以下
Ｎ、Ｐ、Ｓはいずれも鋼中に固溶してＥｌ、ｒ値を低下
させる。よって含有量は少ない程良く、それぞれ0.005
％、0.01％、0.005 ％以下とした。
Ｏ：0.005 ％以下
Ｏも鋼中に過剰に存在すると酸化物として析出し、Ｅ
ｌ、ｒ値を低下させる。よって含有量の上限を0.005 ％
とする。
【００１１】Mn：0.03〜0.30％
Mnは鋼中に固溶するＳと化合し、析出して無害化するた
めに有効であり、少量が固溶することによっては材質上
影響は少ない。しかし、0.30％を超えると徐々にＥｌ、
ｒ値を低下させる。よって、0.03％以上0.30％以下とす
る。
Si：0.10％以下
SiもMn同様に多量に鋼中に存在するとＥｌ、ｒ値を低下
させ、また、めっき濡れ性を阻害する。よって含有量の
上限を0.10％とする。
【００１２】
Ti：0.010 ％以下、Nb：0.03％以下で、かつ Ｃ／12≦Nb／93≦Ｃ／2
Ti、NbはＣと結合してTiＣ、NbＣとして析出し、加工性
を向上する。しかし、0.010 ％を超えるTi添加は合金化
溶融亜鉛めっき鋼板の外観にライン方向の濃淡むらを生
じ易く、上限を0.010 ％とする。よって、主にNbを添加
するが、その添加はＣとの原子比で１以上が必要であ
る。ただし、過剰の添加は経済性を損ねるため上限は原
子比６とする。即ち、Ｃ／12≦Nb／93≦Ｃ／2 で規定さ
れる。また、Nb添加量の上限は0.03％とする。
【００１３】Al：0.01〜0.10％
AlはTi、Nbを添加する際に、これらが酸化して損失する
ことを防止するために0.01％以上必要であり、また鋼中
のＮ、Ｓと化合してこれらを無害化する効果がある。し
かし、0.10％を超えて添加しても効果は飽和し、経済的
でない。
Ｂ：0.001 ％以下
ＢはＧＡ鋼板のスポット溶接連続打点性の向上、耐二次
加工脆性向上の必要に応じ添加出来る。しかし、0.001
％を越える添加ではこれらの効果は飽和し、むしろ材質
の低下を招くため好ましくない。
【００１４】つぎに、熱延、冷延は通常の工程でよい
が、高加工性を得るためには、仕上げ温度はAr3 変態点
前後の 850〜 920℃が好ましく、巻取り温度は 600℃以
上にすることが好ましい。また、冷延においても圧下率
50％以上とすることが好ましい。溶融亜鉛めっきにおい
ては、まず焼鈍還元に先立ち鋼板表面を清浄化するが、
この方法としては脱脂、酸洗等によっても燃焼によって
も良い。材質確保のため焼鈍還元温度は再結晶温度以上
が必要であるが、生産性の点から 780℃以上とすること
が好ましい。雰囲気としては数％〜数十％のＮ2 を含む
Ｈ2 を用いるのが適当であり、露点は 0℃以下とするこ
とが好ましい。
【００１５】焼鈍還元後の鋼板は還元ガス中で冷却後そ
のまま溶融亜鉛めっき浴に導入されるが、その浴成分及
び温度は以下のように決定される。
浴中Al、Pb濃度
本発明ではめっき条件によって溶融亜鉛めっき合金層を
制御してめっき外観と耐パウダリング性を確保する。そ
のためにはめっき浴Al濃度を重量比で0.12〜0.18％とす
ることが必要である。0.12％未満においては後の合金化
時にΓ相が生成し易くなり、耐パウダリング性を劣化
し、0.18％超では合金化が遅くなり、美麗な外観及びΓ
相の生成が抑制できる 550℃の合金化温度では合金化時
間が極端に長くなり生産性を低下させる。Pbについては
合金化に影響はないが、耐食性の問題から0.1 ％以下が
良い。
【００１６】浴温、侵入板温
浴温〔ＴＢ（℃）〕、侵入板温〔ＴＳ（℃）〕は共に高
いと合金化後の外観が劣化し、Γ相が生成し易くなり、
耐パウダリング性を劣化する傾向にあるが浴のAl濃度
〔ＣAl（重量％）〕が上昇するに従いその傾向は和ら
ぐ。よって、浴温は480℃以下、侵入板温は（浴温＋15
℃）以下とし、かつ、浴Al濃度との間に以下の式を満足
することが必要である。
【００１７】ＴＢ／ＣAl＋ＴＳ≦4000
一方、浴温が 450℃未満では目付け調整のガスワイピン
グが難しくなる。また、侵入板温が 380℃より低温では
溶融亜鉛とのなじみが悪くなり、不めっきを発生する恐
れがある。溶融亜鉛めっき浴浸漬後の鋼板はガスワイピ
ング等により目付け調整を受け合金化される。合金化度
（めっき層中のFe濃度）はη相の残らない 7％以上、Γ
相の生成の少ない12％以下でなければならない。ただ
し、合金化温度が 550℃を超えると合金化度が12％以下
でもΓ相が多くなり、一方、 450℃未満では合金化が極
めて遅くなり生産性上好ましくない。
【００１８】目付量
目付量は耐食性に充分な25g/m2以上、耐パウダリング性
を劣化しない75g/m2以下とする。以上により、高加工性
で外観美麗かつ耐めっき剥離性に優れるＧＡ鋼板が得ら
れるが、さらにプレス成形時の摺動性等の要求に応じ上
層めっき等を行うことができる。
【００１９】次に実施例に基づいて本発明を説明する。
【００２０】
【実施例】めっき装置としては縦型のＣＧＬシミュレー
ターを用い、焼鈍還元ガスには 5％水素含有窒素を用い
て70mm× 180mmの鋼板にめっきを行った。めっきの合金
化処理にはめっき鋼板に直接通電し抵抗発熱量をコント
ロールするタイプの加熱炉を用いた。供試鋼板は真空溶
解炉で溶製し、予め熱延及び冷延を行い板厚 0.7mmに
し、めっき装置装入前に電解脱脂及び塩酸酸洗を行っ
た。熱延の仕上がり温度は 900℃で、一旦冷却後にコイ
ル巻取り後の熱履歴を模して 700℃で 1時間の均熱、冷
却酸洗後に圧下率75％の冷延を行った。
【００２１】表１に供試鋼板の成分及び材質を、表２に
はめっき条件及び合金化処理後のめっき層の組成ならび
に特性を示す。なお、鋼板材質については冷延後の鋼板
を合金化溶融亜鉛めっきサイクルで熱処理して求めた。
めっき鋼板の評価には鋼板材質として伸び率（Ｅｌ）、
ｒ値を、めっき特性としては外観とパウダリング性を評
価した。外観としては焼けムラと筋模様を、パウダリン
グ性の評価は合金化後のめっき鋼板を90度曲げてから曲
げ戻し、剥離しためっきを予め貼付したセロテープで採
取し、その量から５段階で評価した（良１→←５悪）。
【００２２】表２から明らかなように、本発明により高
い加工性と優れた耐めっき剥離性を有する合金化溶融亜
鉛めっき鋼板が製造できることが分かる。
【００２３】
【表１】
【００２４】
【表２】【００２５】
【発明の効果】上記の実施例からも明らかなように、本
発明により高度のプレス加工性と優れた耐めっき剥離性
を有する合金化溶融亜鉛めっき鋼板が製造できる。Description: BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a method for producing an alloyed hot-dip galvanized steel sheet used for an outer panel of an automobile body. 2. Description of the Related Art In recent years, the rust prevention of automobile bodies has been required to be enhanced, and zinc-based surface-treated steel sheets have been used as an improvement measure. Among them, the hot-dip galvanized steel sheet is particularly economically excellent, and furthermore, the heat treatment is used to make the coating layer a Fe-Zn alloy (alloyed hot-dip galvanized steel sheet) to improve the weldability and corrosion resistance after painting. Can be improved. [0003] A galvannealed (hereinafter referred to as GA) steel sheet used for an outer panel of an automobile body is subjected to a high degree of press working for the purpose of enhancing design properties. (Rankford value) is higher. As these solutions, JP-A-3-271354, JP-A-1-184227, JP-A-4-66
As disclosed in Japanese Patent No. 647 and the like, in terms of the material quality of steel materials, a number of reductions of C, N, P, S, etc. in steel and the corresponding optimal hot rolling and cold rolling processes have been proposed. On the other hand, as a characteristic required for a plating layer of a GA steel sheet, it is required that powdering, which cannot be followed by deformation of the steel sheet at the time of working and is powdered and peeled off, does not easily occur. If powdering occurs, it accumulates in the press die to generate a press flaw, and at the same time loses the original corrosion protection of the plating, causing a problem. GA steel plating layer is generally low
It is said that it consists of three Zn-Fe alloy phases of ζ, δ 1 and Γ in order from the Fe content, and it is said that powdering is caused by the Γ phase. [0005] By the way, when a GA steel sheet is manufactured by performing hot dip galvanizing on the above-mentioned reducing materials of C, N, P, S, etc.,
Although it was found that the ductility and r value of the material were satisfactory, it was found that alloying at the grain boundaries of the steel sheet was excessively accelerated, the Γ phase formation amount was increased, and the powdering resistance was reduced. SUMMARY OF THE INVENTION It is an object of the present invention to obtain a high steel material by reducing C, N, P, S in steel, and to provide a beautiful appearance and excellent powdering resistance. To provide a method for producing an alloyed hot-dip galvanized steel sheet. [0007] The gist of the present invention is as follows. That is, by weight ratio, C: 0.0015% or less, Si: 0.10% or less, Mn: 0.03 to 0.30%, Al: 0.01 to 0.10%, P: 0.01% or less, S: 0.005% or less, O: 0.005% or less, N : 0.005% or less, Ti: 0.010 % or less, B: 0.001% or less, and Nb at 0.03% or less, C / 12 ≦ Nb / 93 ≦ C /
2 in the range that satisfies the condition 2, and when the steel sheet substantially consisting of Fe is used as the base steel sheet and the galvannealing is performed by the continuous hot-dip galvanizing apparatus, the Al concentration of the plating bath is 0.12 to 0.18 by weight ratio. % And Pb concentration to 0.1% or less,
Also, the plating bath temperature is set to 450 to 480 ° C, the infiltration temperature of the steel sheet to the plating bath is set to 380 ° C to (bath temperature + 15 ° C), and the plating bath Al concentration [CAl (wt%)] and bath temperature [ TB
(° C.)] and the intruding plate temperature [TS (° C.)] satisfy the following expression: TB / CAl + TS ≦ 4000, and the steel plate is subjected to alloying at a temperature range of 450 to 550 ° C. Fe concentration 7 ~ 12
It is a method for producing an alloyed hot-dip galvanized steel sheet, characterized in that the weight percentage is 25% and the basis weight of the plating is 25 to 75 g / m 2 . The present inventors have found that the influence of C, N, P, S, Ti, and Nb on the composition of the galvanized steel sheet in the galvannealed steel sheet.
As a result of detailed examination of the plating bath composition, alloying temperature, etc., it was clarified that the hot-dip galvanizing conditions before the alloying treatment had a great effect on the galvanizing properties of the hot-dip galvanized steel sheet after the alloying. The production conditions for obtaining an alloyed hot-dip galvanized steel sheet having excellent workability, beautiful appearance, and powdering resistance, which are objects of the present invention, will be described in detail below. First, the composition of a steel plate to be a plating material is determined as follows from the viewpoint of required material and economy. C: 0.0015% or less C is an element that directly determines the strength of steel. In order to obtain extremely high workability [high elongation (El), Rankford value (r value)] which is the object of the present invention, the content is as follows. The smaller the better,
0.0015% or less. N: 0.005% or less, P: 0.01% or less, S:
0.005% or less All of N, P and S form a solid solution in steel and lower the El and r values. Therefore, the smaller the content, the better, each 0.005
%, 0.01%, 0.005% or less. O: 0.005% or less If O is excessively present in steel, it precipitates as an oxide,
Decrease l and r values. Therefore, the upper limit of the content is 0.005%
And Mn: 0.03 to 0.30% Mn is effective for combining with S which forms a solid solution in steel and precipitating it to make it harmless, and a small amount of solid solution has little effect on the material. However, when it exceeds 0.30%, El gradually increases.
Lower the r value. Therefore, it is set to 0.03% or more and 0.30% or less. Si: 0.10% or less Si, when present in steel in a large amount like Mn, lowers the El and r values and inhibits plating wettability. Therefore, the upper limit of the content is set to 0.10%. Ti: 0.010 % or less, Nb: 0.03% or less, and C / 12 ≦ Nb / 93 ≦ C / 2 Ti and Nb combine with C and precipitate as TiC and NbC to improve workability. However, the addition of Ti exceeding 0.010 % tends to cause unevenness in the line direction in the appearance of the galvannealed steel sheet, and the upper limit is made 0.010 %. Therefore, Nb is mainly added, and the addition needs to be at least 1 in atomic ratio with C. However, an excessive addition impairs economic efficiency, so the upper limit is set at 6 in atomic ratio. That is, it is defined as C / 12 ≦ Nb / 93 ≦ C / 2. The upper limit of the amount of Nb added is 0.03%. Al: 0.01 to 0.10% Al must be added in an amount of 0.01% or more in order to prevent Ti and Nb from being oxidized and lost when Ti and Nb are added, and to be combined with N and S in steel. This has the effect of rendering them harmless. However, the effect is saturated even if it exceeds 0.10%, and it is not economical. B: 0.001% or less B can be added as necessary to improve the continuous welding property of spot welding of GA steel sheet and to improve the brittleness resistance in secondary working. But 0.001
%, These effects saturate, and rather deteriorate the material, which is not preferable. Next, hot rolling and cold rolling may be performed in the usual steps, but in order to obtain high workability, the finishing temperature is preferably 850 to 920 ° C. around the Ar 3 transformation point, and the winding temperature is 600 ° C. It is preferable to make the above. Also, the rolling reduction rate in cold rolling
Preferably, it is 50% or more. In hot-dip galvanizing, the steel sheet surface is first cleaned prior to annealing reduction.
This method may be performed by degreasing, pickling, or the like, or by burning. Although the annealing reduction temperature is required to be higher than the recrystallization temperature to secure the material, it is preferable to be 780 ° C. or higher from the viewpoint of productivity. It is suitably used and H 2 containing several% to several tens% of N 2 as an atmosphere, the dew point is preferably set to 0 ℃ or less. The steel sheet after the annealing reduction is cooled and then introduced into a hot dip galvanizing bath in a reducing gas. The bath components and temperature are determined as follows. Al and Pb concentrations in bath In the present invention, the hot-dip galvanized alloy layer is controlled by the plating conditions to ensure the plating appearance and powdering resistance. For that purpose, it is necessary to set the plating bath Al concentration to 0.12 to 0.18% by weight. If it is less than 0.12%, a phase is likely to be formed during alloying later, and the powdering resistance will be degraded. If it exceeds 0.18%, alloying will be slow, resulting in a beautiful appearance and
At an alloying temperature of 550 ° C where the formation of phases can be suppressed, the alloying time becomes extremely long and the productivity decreases. Pb does not affect alloying, but is preferably 0.1% or less due to corrosion resistance. If both the bath temperature and the penetration plate temperature [TB (° C.)] and the penetration plate temperature [TS (° C.)] are high, the appearance after alloying is deteriorated, and the Δ phase is easily formed,
The powdering resistance tends to deteriorate, but the tendency is reduced as the Al concentration [CAl (% by weight)] of the bath increases. Therefore, the bath temperature is 480 ° C or less, and the intrusion plate temperature is (bath temperature +15
° C) or less, and the following formula must be satisfied between the temperature and the bath Al concentration. TB / CAl + TS ≦ 4000 On the other hand, if the bath temperature is lower than 450 ° C., it is difficult to perform gas wiping for adjusting the basis weight. If the infiltration plate temperature is lower than 380 ° C, the penetration with the molten zinc becomes poor, and non-plating may occur. The steel sheet after immersion in the hot-dip galvanizing bath is alloyed by adjusting the basis weight by gas wiping or the like. The degree of alloying (Fe concentration in the plating layer) is 7% or more with no η phase remaining.
Must be less than 12% with little phase formation. However, if the alloying temperature exceeds 550 ° C, the amount of the Γ phase increases even if the degree of alloying is 12% or less, while if it is less than 450 ° C, the alloying becomes extremely slow, which is not preferable in terms of productivity. The weight per unit area is not less than 25 g / m 2 sufficient for corrosion resistance and not more than 75 g / m 2 which does not deteriorate the powdering resistance. As described above, a GA steel sheet having high workability, beautiful appearance, and excellent plating peeling resistance can be obtained, but upper plating and the like can be further performed according to the requirements of slidability during press molding. Next, the present invention will be described based on examples. EXAMPLE A vertical CGL simulator was used as a plating apparatus, and a steel sheet of 70 mm × 180 mm was plated using 5% hydrogen-containing nitrogen as an annealing reducing gas. For the alloying treatment of the plating, a heating furnace of a type in which electric current was directly applied to the plated steel sheet to control the heating value of the resistance was used. The test steel sheet was melted in a vacuum melting furnace, hot rolled and cold rolled in advance to a sheet thickness of 0.7 mm, and subjected to electrolytic degreasing and hydrochloric acid pickling before being charged into the plating apparatus. The finishing temperature of hot rolling was 900 ° C, and after cooling, the steel sheet was soaked at 700 ° C for 1 hour to imitate the heat history after coil winding, and cold-rolled at a rolling reduction of 75% after cooling and pickling. Table 1 shows the components and materials of the test steel sheet, and Table 2 shows the plating conditions and the composition and properties of the plated layer after the alloying treatment. The steel sheet material was determined by heat-treating the cold-rolled steel sheet in a galvannealing cycle.
For evaluation of plated steel sheet, elongation rate (El) as the steel sheet material,
The r value was used to evaluate the appearance and powdering properties as plating characteristics. The appearance of burn unevenness and streak pattern was evaluated. Powdering property was evaluated by bending the alloyed steel sheet by 90 degrees and then bending it back, and then using a scotch tape to which the peeled plating had been applied in advance, and evaluating the amount on a 5-point scale. (Good 1 → ← 5 bad) As is clear from Table 2, it can be seen that the present invention can produce an alloyed hot-dip galvanized steel sheet having high workability and excellent anti-plating resistance. [Table 1] [Table 2] As is clear from the above examples, according to the present invention, an alloyed hot-dip galvanized steel sheet having a high degree of press workability and excellent plating peeling resistance can be manufactured.
───────────────────────────────────────────────────── フロントページの続き (56)参考文献 特開 昭62−185834（ＪＰ，Ａ) 特開 昭58−110659（ＪＰ，Ａ) 特開 平３−271354（ＪＰ，Ａ) 特開 平４−276053（ＪＰ，Ａ) 特開 平１−184227（ＪＰ，Ａ) 特開 平６−256903（ＪＰ，Ａ) (58)調査した分野(Int.Cl.7，ＤＢ名) C23C 2/00 - 2/40 ──────────────────────────────────────────────────続 き Continuation of the front page (56) References JP-A-62-185834 (JP, A) JP-A-58-110659 (JP, A) JP-A-3-271354 (JP, A) JP-A-4- 276053 (JP, A) JP-A-1-184227 (JP, A) JP-A-6-256903 (JP, A) (58) Fields investigated (Int. Cl. 7 , DB name) C23C 2/00-2 / 40
Claims (1)
2 を満足する範囲で含み、残部実質的にFeからなる鋼板
をめっき素地鋼板として、連続式溶融亜鉛めっき装置で
合金化溶融亜鉛めっきを行うに際して、 めっき浴のAl濃度を重量比で0.12〜0.18％、Pb濃度を0.
1 ％以下とし、 かつ、めっき浴温を 450〜 480℃とし、 かつ、めっき浴への鋼板浸入温度を 380℃〜( 浴温＋15
℃) とし、 かつ、めっき浴Al濃度〔ＣAl（重量％）〕と浴温〔ＴＢ
（℃）〕と侵入板温〔ＴＳ（℃）〕が次式 ＴＢ／ＣAl＋ＴＳ≦4000 を満足させ、 かつ、鋼板到達温度が 450〜 550℃の温度範囲で合金化
処理を行い、めっき層中のFe濃度を 7〜12重量％とし、 かつ、めっきの目付量を25〜75g/m2とすることを特徴と
する合金化溶融亜鉛めっき鋼板の製造方法。(57) [Claims] [Claim 1] By weight ratio, C: 0.0015% or less, Si: 0.10% or less, Mn: 0.03 to 0.30%, Al: 0.01 to 0.10%, P: 0.01% or less, S: 0.005% or less, O: 0.005% or less, N: 0.005% or less, Ti: 0.010 % or less, B: 0.001% or less, and Nb of 0.03% or less, C / 12 ≦ Nb / 93 ≦ C /
When the steel sheet consisting essentially of Fe is used as the base metal sheet and alloying hot-dip galvanizing is performed using a continuous hot-dip galvanizing apparatus, the Al concentration of the plating bath is 0.12 to 0.18 by weight. %, Pb concentration to 0.
1% or less, and the plating bath temperature is 450 to 480 ° C, and the steel sheet penetration temperature into the plating bath is 380 ° C (bath temperature + 15
° C) and the plating bath Al concentration [CAl (% by weight)] and the bath temperature [TB
(° C)] and the intruding plate temperature [TS (° C)] satisfy the following formula: TB / CAl + TS ≦ 4000, and the alloying process is performed in the temperature range of the steel plate reaching temperature of 450 to 550 ° C. A method for producing an alloyed hot-dip galvanized steel sheet, wherein the Fe concentration is 7 to 12% by weight and the basis weight of plating is 25 to 75 g / m 2 .
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP01047994A JP3382697B2 (en) | 1994-02-01 | 1994-02-01 | Manufacturing method of galvannealed steel sheet |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP01047994A JP3382697B2 (en) | 1994-02-01 | 1994-02-01 | Manufacturing method of galvannealed steel sheet |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH07216526A JPH07216526A (en) | 1995-08-15 |
| JP3382697B2 true JP3382697B2 (en) | 2003-03-04 |
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ID=11751300
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| JP01047994A Expired - Fee Related JP3382697B2 (en) | 1994-02-01 | 1994-02-01 | Manufacturing method of galvannealed steel sheet |
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US6368728B1 (en) * | 1998-11-18 | 2002-04-09 | Kawasaki Steel Corporation | Galvannealed steel sheet and manufacturing method |
| JP5011953B2 (en) * | 2006-10-26 | 2012-08-29 | 住友金属工業株式会社 | Alloyed hot-dip galvanized steel sheet and method for producing the same |
| JP5167867B2 (en) * | 2008-03-03 | 2013-03-21 | 新日鐵住金株式会社 | Alloyed hot-dip galvanized steel sheet with excellent surface properties and method for producing the same |
| US11913118B2 (en) | 2018-03-01 | 2024-02-27 | Nucor Corporation | Zinc alloy coated press-hardenable steels and method of manufacturing the same |
| WO2019169199A1 (en) * | 2018-03-01 | 2019-09-06 | Nucor Corporation | Zinc-based alloy coating for steel and methods |
| JP2021014605A (en) | 2019-07-10 | 2021-02-12 | 株式会社神戸製鋼所 | Hot-dip galvanized steel sheet and method for manufacturing alloyed hot-dip galvanized steel sheet |
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