JPH04202631A - Production of galvannealed p-containing high tensile strength steel sheet - Google Patents
Production of galvannealed p-containing high tensile strength steel sheetInfo
- Publication number
- JPH04202631A JPH04202631A JP32954790A JP32954790A JPH04202631A JP H04202631 A JPH04202631 A JP H04202631A JP 32954790 A JP32954790 A JP 32954790A JP 32954790 A JP32954790 A JP 32954790A JP H04202631 A JPH04202631 A JP H04202631A
- Authority
- JP
- Japan
- Prior art keywords
- steel sheet
- oxidation
- zone
- hot
- tensile 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
Links
- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 40
- 239000010959 steel Substances 0.000 title claims abstract description 40
- 238000004519 manufacturing process Methods 0.000 title claims description 11
- 230000003647 oxidation Effects 0.000 claims abstract description 37
- 238000007254 oxidation reaction Methods 0.000 claims abstract description 37
- 238000007747 plating Methods 0.000 claims abstract description 19
- 239000001257 hydrogen Substances 0.000 claims abstract description 12
- 229910052739 hydrogen Inorganic materials 0.000 claims abstract description 12
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 claims abstract description 10
- 238000000137 annealing Methods 0.000 claims abstract description 8
- 238000002485 combustion reaction Methods 0.000 claims abstract description 7
- 229910001335 Galvanized steel Inorganic materials 0.000 claims description 15
- 239000008397 galvanized steel Substances 0.000 claims description 15
- 238000000034 method Methods 0.000 claims description 14
- 238000005275 alloying Methods 0.000 abstract description 19
- 238000010438 heat treatment Methods 0.000 abstract description 10
- 229910045601 alloy Inorganic materials 0.000 abstract description 7
- 239000000956 alloy Substances 0.000 abstract description 7
- 229910052725 zinc Inorganic materials 0.000 abstract description 6
- 239000011701 zinc Substances 0.000 abstract description 6
- HCHKCACWOHOZIP-UHFFFAOYSA-N Zinc Chemical compound [Zn] HCHKCACWOHOZIP-UHFFFAOYSA-N 0.000 abstract description 4
- 238000007598 dipping method Methods 0.000 abstract 1
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 7
- 230000001590 oxidative effect Effects 0.000 description 6
- 238000005246 galvanizing Methods 0.000 description 4
- 238000007796 conventional method Methods 0.000 description 3
- 230000000694 effects Effects 0.000 description 3
- 239000000463 material Substances 0.000 description 3
- 238000004381 surface treatment Methods 0.000 description 3
- UQSXHKLRYXJYBZ-UHFFFAOYSA-N Iron oxide Chemical compound [Fe]=O UQSXHKLRYXJYBZ-UHFFFAOYSA-N 0.000 description 2
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 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
- 238000010586 diagram Methods 0.000 description 2
- 238000011156 evaluation Methods 0.000 description 2
- 150000002431 hydrogen Chemical class 0.000 description 2
- 229910052742 iron Inorganic materials 0.000 description 2
- 239000001301 oxygen Substances 0.000 description 2
- 229910052760 oxygen Inorganic materials 0.000 description 2
- 239000002344 surface layer Substances 0.000 description 2
- 229910001295 No alloy Inorganic materials 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 239000003795 chemical substances by application Substances 0.000 description 1
- 239000010960 cold rolled steel Substances 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 239000007789 gas Substances 0.000 description 1
- JEIPFZHSYJVQDO-UHFFFAOYSA-N iron(III) oxide Inorganic materials O=[Fe]O[Fe]=O JEIPFZHSYJVQDO-UHFFFAOYSA-N 0.000 description 1
- 239000010410 layer Substances 0.000 description 1
- 239000007788 liquid Substances 0.000 description 1
- 239000000203 mixture Substances 0.000 description 1
- 229910052759 nickel Inorganic materials 0.000 description 1
- 239000003921 oil Substances 0.000 description 1
- 230000002265 prevention Effects 0.000 description 1
- 239000010731 rolling oil Substances 0.000 description 1
- 239000004576 sand Substances 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 239000002436 steel type Substances 0.000 description 1
- 238000005728 strengthening Methods 0.000 description 1
Landscapes
- Coating With Molten Metal (AREA)
- Heat Treatment Of Sheet Steel (AREA)
- Heat Treatment Of Strip Materials And Filament Materials (AREA)
Abstract
Description
【発明の詳細な説明】
(産業上の利用分野)
本発明はP含有高張力合金化溶融亜鉛めっき鋼板の製造
方法に関するもので、更に詳しくは、鋼中P濃度が0.
04%以上のP含有鋼板に対して、合金化溶融亜鉛めっ
き鋼板の特性を確保するための急速酸化による前焼鈍、
その後、水素含有雰囲気中での焼鈍後溶融めっきする、
P含有高張カ溶融亜鉛めっき鋼板の製造方法にある。DETAILED DESCRIPTION OF THE INVENTION (Field of Industrial Application) The present invention relates to a method for manufacturing a P-containing high tensile strength alloyed hot-dip galvanized steel sheet, and more specifically, the present invention relates to a method for producing a P-containing high-tensile alloyed galvanized steel sheet, and more specifically, the present invention relates to a method for producing a P-containing high-tensile alloyed galvanized steel sheet, and more specifically, the present invention relates to a method for producing a P-containing high-tensile alloyed galvanized steel sheet.
Pre-annealing by rapid oxidation to ensure the properties of alloyed hot-dip galvanized steel sheets for steel sheets containing 4% or more of P;
Then, hot-dip plating is performed after annealing in a hydrogen-containing atmosphere.
A method for producing a P-containing hypertonic hot-dip galvanized steel sheet.
(従来の技術)
近年、自動車用鋼板として用いられる冷延鋼板には、車
体の軽量化及び安全性の向上並びに耐食性の見地から、
プレス加工性に優れることのほかに高強度であり、かつ
耐食性が要求され供給鋼材の表面処理化が強く要求され
る状況にある。このなかで特に最近では、高張力鋼板の
表面処理化要求が高まりつつある。この高張力鋼板の防
錆力向上を主目的とした表面処理方法としては、生産性
の点から容易に厚メツキ化が可能なゼンジマー式溶融亜
鉛メツキ法がある。このゼンジマー式溶融亜鉛メツキ法
の場合、無酸化炉で生成された鉄酸化膜が、それ以降の
還元帯で還元された後、鋼中の易酸化元素であるSL、
Mn、P、AQが鋼板表面で選択的に酸化され、これに
より濃化勾配が生じるために、表面に濃化していく。こ
れらの元素のうち、Pは、鋼板表面にPOxの皮膜を形
成し、合金化特性を著しく阻害する(局部的に合金ムラ
が発生する)。これを改善する従来の方法としては、焼
鈍前に−Fe、ZnまたはN1をプレメツキする方法及
び酸素を含む酸化炉中で鋼板表面の圧延油を除去し、適
度な酸化膜を形成せしめた後、水素を含む雰囲気中で還
元焼鈍後、炉内で板温を調節し、めっきする方法が既に
特開昭55−122865号公報で知られている。すな
わち酸素を含まない無酸化炉方式では、鋼表面の油を除
去することが出来るが、酸化性雰囲気が弱いため、酸化
され易いSj、 Mn、 A Qが表面に拡散酸化され
るため、これらの酸化物が鋼表面を形成する。これらの
酸化物は還元炉中では還元されずめっきの濡れ不良、め
っき密着不良の原因となる。そのために鋼板の表面に酸
化膜の厚み400〜10,000人 になるように酸化
した後、水素を含む雰囲気で焼鈍し、溶融めっきすると
いうものである。(Prior art) In recent years, cold-rolled steel sheets used as steel sheets for automobiles have been developed from the viewpoint of reducing the weight of car bodies, improving safety, and corrosion resistance.
In addition to excellent press workability, high strength and corrosion resistance are required, and there is a strong demand for surface treatment of supplied steel materials. Particularly recently, there has been an increasing demand for surface treatment of high-strength steel sheets. As a surface treatment method whose main purpose is to improve the rust prevention ability of high-tensile steel sheets, there is the Sendzimer hot-dip galvanizing method, which can easily increase the thickness of the galvanized steel sheet from the viewpoint of productivity. In the case of this Sendzimer hot-dip galvanizing method, the iron oxide film produced in the non-oxidizing furnace is reduced in the subsequent reduction zone, and then SL, an easily oxidizable element in steel,
Mn, P, and AQ are selectively oxidized on the surface of the steel sheet, thereby creating a concentration gradient, so that they become concentrated on the surface. Among these elements, P forms a POx film on the surface of the steel sheet and significantly impedes alloying properties (localized unevenness in alloying occurs). Conventional methods to improve this include a method of pre-plating with -Fe, Zn or N1 before annealing, and a method of removing rolling oil from the surface of the steel sheet in an oxidation furnace containing oxygen to form an appropriate oxide film. A method is already known from JP-A-55-122865, in which after reduction annealing in an atmosphere containing hydrogen, the plate temperature is adjusted in a furnace and plating is performed. In other words, in a non-oxidizing furnace method that does not contain oxygen, oil on the steel surface can be removed, but because the oxidizing atmosphere is weak, Sj, Mn, A, and Q, which are easily oxidized, are diffused and oxidized on the surface. Oxides form the steel surface. These oxides are not reduced in the reduction furnace and cause poor plating wettability and poor plating adhesion. To achieve this, the surface of the steel plate is oxidized to an oxide film thickness of 400 to 10,000 mm, then annealed in an atmosphere containing hydrogen, and then hot-dip plated.
(発明が解決しようとする課題) しかしながら、従来技術である焼鈍前に、F’e。(Problem to be solved by the invention) However, before annealing, which is the prior art, F'e.
ZnまたはNiをプレメツキする方法はプレメツキ皮膜
が不安定であり、炉内雰囲気が汚染されること、また鋼
種によってメツキ液を使11分けなcすればならない等
の困難があり、更に後者の特開昭55−122865号
公報についても上記のように無酸化炉の空気比を高くし
て加熱し、 Fe酸化膜を生成した後、還元加熱すると
、良好なめつき性力1得られるという知見のみであって
、鋼中のPと合金化溶融亜鉛めっき層との関係について
は全く開示されていないこと。更には実際の操業ライン
レこお+するラインスピードを下げ1合金化炉内の在炉
時間を長くすることにより、鋼板全体を合金化させる方
法はあるが、 しかしこの方法では20〜30%のライ
ンスピードを低下させなければならず生産性力1著しく
低下する問題点があった。The method of pre-plating Zn or Ni has difficulties such as the pre-plating film is unstable, the atmosphere inside the furnace is contaminated, and plating liquid must be used depending on the steel type. Regarding Publication No. 55-122865, the only finding is that good plating properties 1 can be obtained by heating with a high air ratio in a non-oxidizing furnace to generate an Fe oxide film and then heating by reduction. However, the relationship between P in the steel and the alloyed hot-dip galvanized layer is not disclosed at all. Furthermore, there is a method of alloying the entire steel plate by lowering the line speed and increasing the time in the alloying furnace. There was a problem in that the speed had to be reduced, resulting in a significant drop in productivity.
そこで、本発明は高生産性のラインにあって、従来法と
は異なる方法により、合金ムラを伴うことなく、安定し
た品位で均一外観の優れた合金イし溶融亜鉛めっき鋼板
を得る方法を提供することにある。Therefore, the present invention provides a method for obtaining an alloy hot-dip galvanized steel sheet with stable quality and uniform appearance without alloy unevenness on a high productivity line using a method different from conventional methods. It's about doing.
(課題を解決するための手段)
上述した問題点を解決し、その目的を達成するために、
本発明の要旨とするところは、鋼中P濃度0.04%以
上のP含有高張力溶融亜鉛めっき鋼板の製造方法におい
て、酸化帯燃焼空気比0.95〜1.10で、かつ予熱
帯を除く酸化帯での平均酸化速度を30人/ see以
上とする急速酸化後、還元帯水素濃度10%以下なる雰
囲気中で焼砂し、溶融めっきすることにある。以下本発
明について詳細に説明する。(Means for solving the problem) In order to solve the above problems and achieve the purpose,
The gist of the present invention is to provide a method for producing P-containing high-strength hot-dip galvanized steel sheets with a P concentration of 0.04% or more in the steel, with an oxidation zone combustion air ratio of 0.95 to 1.10, and a preheating zone. After rapid oxidation with an average oxidation rate of 30 people/see or more in the oxidation zone, the process involves burning sand in an atmosphere with a hydrogen concentration of 10% or less in the reduction zone, followed by hot-dip plating. The present invention will be explained in detail below.
本発明において鋼中P濃度0.04%以上とした理由は
高張力鋼として固溶強化、熱延板の結晶粒を微細化する
作用があり、またコストも安価であるため望ましい元素
である。特にスキンパスに伴う延性劣化を少なくする効
果が大であることから重要な元素であり、 この効果を
もたらすためには、0.04%以上を必要とし、一方0
.15%をこえるとPの適量は脆化、溶接性劣化をもた
らすため最適は0.04〜0.15が望ましい。一方鋼
中にpm度が0.04%以上のP含有鋼の場合には、一
般には離合金化材と呼ばれ、鋼中のSi、 Mn、 A
Q 、 Pなどが鋼板表面の加熱によって、酸化物と
して鋼板表層に拡散されるため、これら酸化物が濃化し
、鋼表面を形成する。これらの酸化物は還元炉中でも還
元されず、合金化特性を阻害し、めっき密着性を悪くす
る。従ってこれら難合金化材を対象とした鋼材について
の溶融亜鉛めっきを高生産性のラインにおいて合金ムラ
なく、シかも均一外観の優れためっきを可能としたこと
にある。そのための条件として、第1に酸化帯燃焼空気
比0.95〜1.10としたこと。第2は本発明の最大
の特徴でもある酸化帯での平均酸化速度を30人/ s
ec以上としたこと。In the present invention, the P concentration in the steel is set to 0.04% or more because it is a desirable element because it has the effect of solid solution strengthening as a high-strength steel and refines the crystal grains of hot-rolled sheets, and is also inexpensive. It is an important element because it is particularly effective in reducing ductility deterioration associated with skin passes.To bring about this effect, 0.04% or more is required, while 0.04% or more is required.
.. If the amount exceeds 15%, an appropriate amount of P causes embrittlement and deterioration of weldability, so the optimum amount is preferably 0.04 to 0.15. On the other hand, in the case of steel containing P with a PM degree of 0.04% or more, it is generally called a dealloying material, and Si, Mn, A in the steel
Q, P, etc. are diffused into the steel plate surface layer as oxides by heating the steel plate surface, so these oxides are concentrated and form the steel surface. These oxides are not reduced even in a reducing furnace, inhibit alloying properties, and impair plating adhesion. Therefore, the present invention has made it possible to hot-dip galvanize steel materials that are difficult to alloy, with no alloying irregularities, and with excellent uniform appearance on a high-productivity line. The first condition for this was that the oxidation zone combustion air ratio was set to 0.95 to 1.10. The second is that the average oxidation rate in the oxidation zone, which is the biggest feature of the present invention, is 30 people/s.
It was set as ec or higher.
第3は還元帯水素濃度10%以下なる雰囲気中で焼鈍し
、溶融めっきしたことにある。すなわち第1条件である
酸化帯燃焼空気比0.95〜1.10としたことは、空
気比0.95未満では、微妙なガス組成の変化で酸化挙
動が大きく変化し、最適目標とする200〜1000人
なる酸化膜を調整することは出来ない。The third reason is that annealing and hot-dip plating were performed in an atmosphere with a reduction zone hydrogen concentration of 10% or less. In other words, the first condition of setting the oxidation zone combustion air ratio to 0.95 to 1.10 is because if the air ratio is less than 0.95, the oxidation behavior will change greatly due to subtle changes in the gas composition. It is not possible to adjust the oxide film of ~1000 people.
また空気比1.10を超えると急激に酸化膜が生成し、
目標酸化膜を容易に越し、これも調整することが困・難
である。従って最適目標とする酸化膜の生成を容易に制
御可能な範囲での空気比であること、次に第2の条件で
ある最大の特徴とする予熱帯を除く酸化帯での平均酸化
速度を30人/see以上としたこと。この理由は、第
1図に示すように従来法Aに示す、例えば20人/Se
C以下の場合には、酸化膜の生成速度が遅いため、鋼板
表面に適度な酸化膜を形成する前に、酸化され易いSi
、 Mn、 A Q 。In addition, when the air ratio exceeds 1.10, an oxide film rapidly forms,
It easily exceeds the target oxide film and is difficult to adjust. Therefore, the air ratio must be within a range that can easily control the production of an oxide film, which is the optimum target, and the second condition is that the average oxidation rate in the oxidation zone, excluding the preheating zone, is 30%. Person/see or more. The reason for this is that, as shown in Fig. 1, for example, 20 people/Se
When the temperature is below C, the rate of formation of an oxide film is slow, so Si, which is easily oxidized, is removed before a suitable oxide film is formed on the steel sheet surface.
, Mn, AQ.
Pが表面に拡散酸化されるため、これらの酸化物が鋼表
面に形成される。従って、これらの酸化物の生成の起ら
ない短時間加熱の急速酸化が必要であることを見出した
ものである。しかも、それに必要な酸化膜から考えて、
第1図に示すB直線である30人/see以上が必要で
ある。これ以上であると酸化され易いSi、 Mn、
A fl 、 P等特にPが表面に拡散酸化されないう
ちに鉄表面にFe酸化膜を形成し、 このFe酸化膜が
その後の鋼中のSi。These oxides are formed on the steel surface because P is diffused and oxidized to the surface. Therefore, it has been discovered that rapid oxidation with short heating time is required, which does not generate these oxides. Moreover, considering the oxide film required for this,
30 people/see, which is the line B shown in FIG. 1, is required. If it is more than this, Si, Mn, which is easily oxidized,
Afl, P, etc. In particular, an Fe oxide film is formed on the iron surface before P diffuses to the surface and is not oxidized, and this Fe oxide film later becomes Si in the steel.
Mn、AQ、P等の酸化を阻止する。その後、この酸化
膜を還元帯水素濃度10%以下なる雰囲気中で焼鈍し、
還元した後、溶融亜鉛浴中を通過させ。Prevents oxidation of Mn, AQ, P, etc. After that, this oxide film is annealed in an atmosphere with a reduction zone hydrogen concentration of 10% or less,
After reduction, it is passed through a molten zinc bath.
エアーワイピングでめっき量を調節して得る。また平均
酸化速度30Å/sec以上の急速酸化をするためには
、鋼板に対して垂直に火炎を噴射するバーナーである、
いわゆる直火式加熱バーナーを用いると、より最適な平
均酸化速度を制御することができる。The amount of plating can be adjusted using air wiping. In addition, in order to perform rapid oxidation with an average oxidation rate of 30 Å/sec or more, a burner that injects flame perpendicularly to the steel plate is used.
By using a so-called direct heating burner, it is possible to control the average oxidation rate more optimally.
(作用)
そして、本発明は前記の構成である、急速酸化すること
により易酸化性元素である、特にPの酸化物が鋼板表層
に濃化することなく、 Fe酸化物のみの生成となり、
容易に還元帯によって還元され合金化特性を阻害するF
e酸化膜がなくなり、合金化溶融亜鉛めっき後の外観の
均一性を図ることができる。(Function) The present invention has the above-mentioned configuration. By rapid oxidation, only Fe oxides are generated without the oxides of P, which is an easily oxidizable element, being concentrated on the surface layer of the steel sheet.
F is easily reduced by the reduction zone and inhibits alloying properties.
e There is no oxide film, and the appearance after alloying hot-dip galvanizing can be made more uniform.
(実施例)
実施例1
高張力60kg1dクラスノハイテン60(C0,10
x。(Example) Example 1 High tension 60kg1d Krasnohyten 60 (C0,10
x.
Si0.6%、 Mn 1.10%、 P O,04%
、 A Qo、03%)を酸化帯燃焼空気比1.05、
平均酸化速度400人/6Secで500℃迄加熱酸化
した後、還元帯水素濃度10%で還元し、その後溶融亜
鉛浴(0,15%AQ、450℃)中を通過させ、エア
ーワイピングでめっき量を180g/rrfに調節した
後合金化処理した。その合金化溶融亜鉛めっき鋼板の合
金化特性を調べた。Si0.6%, Mn 1.10%, PO,04%
, A Qo, 03%), oxidation zone combustion air ratio 1.05,
After heating and oxidizing to 500°C at an average oxidation rate of 400 persons/6 sec, the reduction zone is reduced with a hydrogen concentration of 10%, and then passed through a molten zinc bath (0.15% AQ, 450°C), and the amount of plating is reduced by air wiping. After adjusting the amount to 180 g/rrf, alloying treatment was performed. The alloying properties of the alloyed hot-dip galvanized steel sheets were investigated.
合金化特性はめっき部分の断面写真で評価した。Alloying properties were evaluated using cross-sectional photographs of the plated parts.
その結果第2図に示すように、従来の平均酸化速度20
℃/seeの同一条件にて行ったものと比較すると、第
1表に示すような評価によれば一部合金ムラないし合金
ムラがが多く見られた。これに対し本発明によれば外観
均一、合金ムラが全く見られなかった。As a result, as shown in Figure 2, the average oxidation rate was 20
When compared with those conducted under the same conditions of °C/see, according to the evaluation shown in Table 1, some alloy unevenness or alloy unevenness was observed in many cases. In contrast, according to the present invention, the appearance was uniform and no alloy unevenness was observed.
第1表
実施例2
高張力80kg/cJハイテン80(CO,15%、
Si 1.0%、 Mn 1.5%、 P O,10%
、AQo、02%) を酸化帯燃焼空気比1.05.平
均酸化速度500人/ 12secで500℃迄加熱酸
化した後、還元帯水素濃度5%で還元し、その後溶融亜
鉛浴(0,10AQ460℃)中を通過させ、エアーワ
イピングでめっき量を180 g /alに調節した後
合金化処理した。その合金化溶融亜鉛めっき鋼板の合金
化特性を調べた。その結果めっきの合金化は断面写真か
ら全く合金ムラがなく。Table 1 Example 2 High tensile strength 80 kg/cJ Hi-Ten 80 (CO, 15%,
Si 1.0%, Mn 1.5%, PO, 10%
, AQo, 02%) at an oxidation zone combustion air ratio of 1.05. After heating and oxidizing to 500°C at an average oxidation rate of 500 people/12 seconds, the reduction zone was reduced with a hydrogen concentration of 5%, and then passed through a molten zinc bath (0.10AQ460°C) and air wiped to reduce the plating amount to 180 g/ After adjusting to al, alloying treatment was performed. The alloying properties of the alloyed hot-dip galvanized steel sheets were investigated. As a result, the alloying of the plating shows no alloying unevenness at all as seen from the cross-sectional photograph.
その結果は4点を得た。The result was 4 points.
(発明の効果)
以上述べたように、本発明による平均酸化速度で急速加
熱と酸化を行うことによって、P含有高張力鋼板であっ
ても、合金化溶融亜鉛めっき条件をいたずらに変更する
ことなく、普通鋼と同様の合金化特性が得られ、合金ム
ラめつきを伴うことなく、安定した品位で均一外観の合
金化溶融亜鉛めっき鋼板として具備すべき性能を充分効
率的に得られることにある。(Effects of the Invention) As described above, by performing rapid heating and oxidation at an average oxidation rate according to the present invention, even P-containing high-strength steel sheets can be coated without unnecessarily changing the alloying hot-dip galvanizing conditions. , it is possible to obtain the same alloying properties as ordinary steel, and to efficiently obtain the performance required of an alloyed hot-dip galvanized steel sheet with stable grade and uniform appearance without causing uneven alloy plating. .
第1図は本発明と従来法との生成酸化膜厚と時間との関
係を示す図、第2図は予熱帯を除く酸化帯での平均酸化
速度と合金化特性評価との関係を示す図である。
代理人 弁理士 椎 名 彊
第2図
平tシう一目PイしニマチζiFigure 1 is a diagram showing the relationship between the thickness of the oxide film formed by the present invention and the conventional method and time, and Figure 2 is a diagram showing the relationship between the average oxidation rate in the oxidation zone excluding the preheating zone and evaluation of alloying characteristics. It is. Agent Patent Attorney Akira Shiina
Claims (2)
鉛めっき鋼板の製造方法において、酸化帯燃焼空気比0
.95〜1.10で、かつ予熱帯を除く酸化帯での平均
酸化速度を30Å/sec以上とする急速酸化後、還元
帯水素濃度10%以下なる雰囲気中で焼鈍し、溶融めっ
きすることを特徴とするP含有高張力合金化溶融亜鉛め
っき鋼板の製造方法。(1) In the method for manufacturing high-tensile alloyed hot-dip galvanized steel sheets with a P concentration in steel of 0.04% or more, the combustion air ratio in the oxidation zone is 0.
.. 95 to 1.10 and the average oxidation rate in the oxidation zone excluding the preheating zone is 30 Å/sec or more, followed by annealing in an atmosphere with a hydrogen concentration of 10% or less in the reduction zone, followed by hot-dip plating. A method for producing a P-containing high-tensile alloyed hot-dip galvanized steel sheet.
するバーナーを用いて急速酸化した後、還元帯水素濃度
10%以下なる雰囲気中で焼鈍し、溶融めっきする請求
項第1項記載のP含有高張力合金化溶融亜鉛めっき鋼板
の製造方法。(2) The oxidation zone is rapidly oxidized using a burner that injects flame perpendicularly to the steel plate, and then the steel plate is annealed in an atmosphere with a hydrogen concentration of 10% or less, and hot-dip plated. The method for producing the P-containing high tensile strength alloyed galvanized steel sheet.
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP2329547A JP2587725B2 (en) | 1990-11-30 | 1990-11-30 | Method for producing P-containing high tensile alloyed hot-dip galvanized steel sheet |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP2329547A JP2587725B2 (en) | 1990-11-30 | 1990-11-30 | Method for producing P-containing high tensile alloyed hot-dip galvanized steel sheet |
Publications (2)
Publication Number | Publication Date |
---|---|
JPH04202631A true JPH04202631A (en) | 1992-07-23 |
JP2587725B2 JP2587725B2 (en) | 1997-03-05 |
Family
ID=18222579
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
JP2329547A Expired - Lifetime JP2587725B2 (en) | 1990-11-30 | 1990-11-30 | Method for producing P-containing high tensile alloyed hot-dip galvanized steel sheet |
Country Status (1)
Country | Link |
---|---|
JP (1) | JP2587725B2 (en) |
Cited By (11)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH0681095A (en) * | 1992-09-01 | 1994-03-22 | Nippon Steel Corp | Production of p-containing high strength galvannealaed steel sheet |
JPH06192807A (en) * | 1992-12-28 | 1994-07-12 | Nippon Steel Corp | P-containing high strength galvannealed steel sheet |
WO2006068169A1 (en) * | 2004-12-21 | 2006-06-29 | Kabushiki Kaisha Kobe Seiko Sho | Method and facility for hot dip zinc plating |
WO2012169653A1 (en) | 2011-06-07 | 2012-12-13 | Jfeスチール株式会社 | High-strength hot-dipped galvanized steel sheet having excellent plating adhesion, and method for producing same |
WO2013157146A1 (en) | 2012-04-17 | 2013-10-24 | Jfeスチール株式会社 | Method for producing alloyed hot-dip galvanized steel sheet having excellent adhesion to plating and excellent sliding properties |
WO2014136417A1 (en) | 2013-03-05 | 2014-09-12 | Jfeスチール株式会社 | High-strength hot-dip galvanized steel sheet and process for manufacturing same |
WO2014188697A1 (en) | 2013-05-21 | 2014-11-27 | Jfeスチール株式会社 | Method for manufacturing high-strength alloyed hot-dip galvanized steel plate |
WO2015087549A1 (en) | 2013-12-13 | 2015-06-18 | Jfeスチール株式会社 | Method for manufacturing high-strength hot-dip galvanized steel sheet |
KR20170039733A (en) | 2014-09-08 | 2017-04-11 | 제이에프이 스틸 가부시키가이샤 | Method and apparatus for producing high-strength hot-dipped galvanized steel sheet |
WO2018079124A1 (en) | 2016-10-25 | 2018-05-03 | Jfeスチール株式会社 | Method for producing high strength hot-dip galvanized steel sheet |
KR20180111931A (en) | 2016-03-11 | 2018-10-11 | 제이에프이 스틸 가부시키가이샤 | METHOD FOR MANUFACTURING STRENGTH OF HIGH-STRENGTH HOT WATER |
Citations (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS5344141A (en) * | 1976-10-01 | 1978-04-20 | Cii Honeywell Bull | Recorded data processor |
JPS55131167A (en) * | 1979-03-30 | 1980-10-11 | Sumitomo Metal Ind Ltd | High tensile alloyed zinc-plated steel sheet |
-
1990
- 1990-11-30 JP JP2329547A patent/JP2587725B2/en not_active Expired - Lifetime
Patent Citations (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS5344141A (en) * | 1976-10-01 | 1978-04-20 | Cii Honeywell Bull | Recorded data processor |
JPS55131167A (en) * | 1979-03-30 | 1980-10-11 | Sumitomo Metal Ind Ltd | High tensile alloyed zinc-plated steel sheet |
Cited By (22)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH0681095A (en) * | 1992-09-01 | 1994-03-22 | Nippon Steel Corp | Production of p-containing high strength galvannealaed steel sheet |
JP2700515B2 (en) * | 1992-09-01 | 1998-01-21 | 新日本製鐵株式会社 | Method for producing high strength galvannealed steel sheet containing P |
JPH06192807A (en) * | 1992-12-28 | 1994-07-12 | Nippon Steel Corp | P-containing high strength galvannealed steel sheet |
WO2006068169A1 (en) * | 2004-12-21 | 2006-06-29 | Kabushiki Kaisha Kobe Seiko Sho | Method and facility for hot dip zinc plating |
US8216695B2 (en) | 2004-12-21 | 2012-07-10 | Kobe Steel, Ltd. | Method and facility for hot dip zinc plating |
WO2012169653A1 (en) | 2011-06-07 | 2012-12-13 | Jfeスチール株式会社 | High-strength hot-dipped galvanized steel sheet having excellent plating adhesion, and method for producing same |
US9677163B2 (en) | 2011-06-07 | 2017-06-13 | Jfe Steel Corporation | High strength galvanized steel sheet excellent in terms of coating adhesiveness and method for manufacturing the same |
WO2013157146A1 (en) | 2012-04-17 | 2013-10-24 | Jfeスチール株式会社 | Method for producing alloyed hot-dip galvanized steel sheet having excellent adhesion to plating and excellent sliding properties |
KR20140138245A (en) | 2012-04-17 | 2014-12-03 | 제이에프이 스틸 가부시키가이샤 | Method for producing alloyed hot-dip galvanized steel sheet having excellent adhesion to plating and excellent sliding properties |
WO2014136417A1 (en) | 2013-03-05 | 2014-09-12 | Jfeスチール株式会社 | High-strength hot-dip galvanized steel sheet and process for manufacturing same |
WO2014188697A1 (en) | 2013-05-21 | 2014-11-27 | Jfeスチール株式会社 | Method for manufacturing high-strength alloyed hot-dip galvanized steel plate |
KR20150136113A (en) | 2013-05-21 | 2015-12-04 | 제이에프이 스틸 가부시키가이샤 | Method for manufacturing high-strength alloyed hot-dip galvanized steel plate |
US10087500B2 (en) | 2013-05-21 | 2018-10-02 | Jfe Steel Corporation | Method for manufacturing high-strength galvannealed steel sheet |
WO2015087549A1 (en) | 2013-12-13 | 2015-06-18 | Jfeスチール株式会社 | Method for manufacturing high-strength hot-dip galvanized steel sheet |
KR20160071423A (en) | 2013-12-13 | 2016-06-21 | 제이에프이 스틸 가부시키가이샤 | Method for manufacturing high-strength hot-dip galvanized steel sheet |
US10138530B2 (en) | 2013-12-13 | 2018-11-27 | Jfe Steel Corporation | Method for producing high-strength galvannealed steel sheets |
KR20170039733A (en) | 2014-09-08 | 2017-04-11 | 제이에프이 스틸 가부시키가이샤 | Method and apparatus for producing high-strength hot-dipped galvanized steel sheet |
KR20180111931A (en) | 2016-03-11 | 2018-10-11 | 제이에프이 스틸 가부시키가이샤 | METHOD FOR MANUFACTURING STRENGTH OF HIGH-STRENGTH HOT WATER |
US10988836B2 (en) | 2016-03-11 | 2021-04-27 | Jfe Steel Corporation | Method for producing high-strength galvanized steel sheet |
WO2018079124A1 (en) | 2016-10-25 | 2018-05-03 | Jfeスチール株式会社 | Method for producing high strength hot-dip galvanized steel sheet |
KR20190057335A (en) | 2016-10-25 | 2019-05-28 | 제이에프이 스틸 가부시키가이샤 | METHOD FOR MANUFACTURING STRENGTH OF HIGH-STRENGTH HOT WATER |
US11535922B2 (en) | 2016-10-25 | 2022-12-27 | Jfe Steel Corporation | Method for manufacturing high-strength galvanized steel sheet |
Also Published As
Publication number | Publication date |
---|---|
JP2587725B2 (en) | 1997-03-05 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
JP7330104B2 (en) | Method for producing steel strip with aluminum alloy coating layer | |
JPH04202630A (en) | Production of hot-dip galvanized high tensile strength steel sheet of high si content excellent in adhesive strength of plating | |
JP3956550B2 (en) | Method for producing high-strength hot-dip galvanized steel sheet with excellent balance of strength and ductility | |
JPH04202631A (en) | Production of galvannealed p-containing high tensile strength steel sheet | |
JP2707928B2 (en) | Hot-dip galvanizing method for silicon-containing steel sheet | |
JP3835083B2 (en) | Cold-rolled steel sheet, hot-dip galvanized steel sheet, and production method | |
KR101428151B1 (en) | Zn-coated hot rolled steel sheet having high mn and method for manufacturing the same | |
JP2530939B2 (en) | Method for manufacturing high-strength hot-dip galvanized steel sheet containing high Si | |
JP2023525519A (en) | Steel annealing method | |
JP5098190B2 (en) | Manufacturing method of high strength hot dip galvanized steel sheet | |
JP2023182581A (en) | Hot-dipped steel sheet excellent in corrosion resistance and processability, and method for manufacturing the same | |
JPH04276057A (en) | Manufacture of high si-containing high tensile strength galvannealed steel sheet having good plating adhesion | |
JP2964911B2 (en) | Alloying hot-dip galvanizing method for P-added high-strength steel | |
JPH09176815A (en) | High strength hot dip galvanized steel sheet excellent in plating adhesion | |
JP2002030403A (en) | Hot dip galvannealed steel sheet and its production method | |
JPH03271354A (en) | Production of galvannealed steel sheet | |
JP3581862B2 (en) | Method for producing hot-dip Al-Zn-based plated steel sheet | |
JPH11140587A (en) | Galvannealed steel sheet excellent in plating adhesion | |
JPH03294463A (en) | Production of alloyed hot-galvanized steel sheet | |
JP2618308B2 (en) | High Si content High tensile galvanized steel sheet | |
JPH06158254A (en) | Manufacture of hot-dip galvannealed steel sheet | |
JP3598889B2 (en) | Method for producing hot-dip galvanized steel sheet and alloyed hot-dip galvanized steel sheet | |
JP2001262303A (en) | Method for producing alloyed galvanized steel sheet and galvannealed steel sheet excellent in hot dip metal coated property | |
JPH046259A (en) | Galvannealed steel sheet excellent in workability and its production | |
JP7401857B2 (en) | Manufacturing method of hot-dip galvanized steel sheet |
Legal Events
Date | Code | Title | Description |
---|---|---|---|
FPAY | Renewal fee payment (event date is renewal date of database) |
Free format text: PAYMENT UNTIL: 20081205 Year of fee payment: 12 |
|
FPAY | Renewal fee payment (event date is renewal date of database) |
Free format text: PAYMENT UNTIL: 20081205 Year of fee payment: 12 |
|
FPAY | Renewal fee payment (event date is renewal date of database) |
Free format text: PAYMENT UNTIL: 20091205 Year of fee payment: 13 |
|
FPAY | Renewal fee payment (event date is renewal date of database) |
Free format text: PAYMENT UNTIL: 20101205 Year of fee payment: 14 |
|
EXPY | Cancellation because of completion of term |