JPS5845322A - Production of painted steel plate having paint baking hardenability - Google Patents
Production of painted steel plate having paint baking hardenabilityInfo
- Publication number
- JPS5845322A JPS5845322A JP14498781A JP14498781A JPS5845322A JP S5845322 A JPS5845322 A JP S5845322A JP 14498781 A JP14498781 A JP 14498781A JP 14498781 A JP14498781 A JP 14498781A JP S5845322 A JPS5845322 A JP S5845322A
- Authority
- JP
- Japan
- Prior art keywords
- less
- steel plate
- plate
- baking
- steel
- 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
Classifications
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Mechanical Engineering (AREA)
- Physics & Mathematics (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Application Of Or Painting With Fluid Materials (AREA)
- Heat Treatment Of Steel (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】
本発明は耐食性構造物に用いられる塗装焼付硬化性と高
耐食性とを兼ね備え九表面処理鋼板の製造方法を提供せ
んとするものである。DETAILED DESCRIPTION OF THE INVENTION The present invention aims to provide a method for manufacturing a surface-treated steel sheet that has both paint-baking hardenability and high corrosion resistance and is used in corrosion-resistant structures.
現在、自動車業界が直面している技術的ｌｌ勉は省エネ
ルギーの観点からの燃費規制、乗員保膜のための安全規
制、省資源、省エネルギーのための防錆規制および積境
面の１！謂からの騒音規制、排ガス規制をクリヤーする
車を作シ出すことである。Currently, the automobile industry is facing technical challenges such as fuel efficiency regulations from the perspective of energy conservation, safety regulations for passenger protective membranes, rust prevention regulations for resource and energy conservation, and one of the most important issues in terms of loading and unloading surfaces. The goal is to create a car that meets the so-called noise regulations and exhaust gas regulations.
これを材料面から言うと、燃費規制、安全規制の面から
は高強直鋼板が、また、防錆規制の面からは表面処理鋼
板が必要とされており、さらにそれらの両者の性能管兼
ね備えた高強度表面処理鋼板が今ｖｋますます重要に々
ると思われる。From a materials perspective, high-strength, straight steel sheets are required from the standpoint of fuel efficiency and safety regulations, and surface-treated steel sheets are required from the standpoint of anti-corrosion regulations. It seems that high-strength surface-treated steel sheets are now becoming increasingly important.
現在高強度冷延鋼板において特に注目嘔れているのが、
成形前は軟質で加工が容易であると同時に、加工後の塗
装焼付によって強度が著しく上昇するという塗装焼付硬
化性鋼板である。仁の塗装焼付硬化性は銅板中に強制固
溶されたＣによる歪時効強化に依っている。What is currently attracting particular attention in high-strength cold-rolled steel sheets is
It is a paint-bake-hardenable steel sheet that is soft and easy to process before forming, and at the same time, its strength increases significantly by baking the paint after forming. The paint baking hardenability of nickel depends on strain aging strengthening due to C that is forcibly dissolved in the copper plate.
一方、高耐食性鋼板としては溶融亜鉛メッキ鋼板、電気
亜鉛メッキ鋼板、合金化処理溶融亜鉛メ、キ鋼板、Ｚ！
ｌ −Ｎ１等の合金電気亜鉛メッキ鋼板等種々の鋼板が
あるが、現在非常に耐食性の優れた鋼板として主として
金属亜鉛゛粉末を含む有機系被膜を塗装し２００〜３０
０℃で焼付する鋼板が注目されている。特に塗装鋼板の
下地として、ｚｎ−ＮｉやＺｎ −Ｎｉ −Ｃｒもしく
はＺｎ −Ｎｉ −Ｃｒ −Ｆｅ等の合金電気亜鉛メッ
キ鋼板を用いると、耐食性に加え耐ノ・クリ性等のプレ
ス成形性にも優ｔ″Ｉた屯のとなる。On the other hand, highly corrosion-resistant steel sheets include hot-dip galvanized steel sheets, electrogalvanized steel sheets, alloyed hot-dip galvanized steel sheets, Z!
There are various steel sheets such as alloy electrogalvanized steel sheets such as L-N1, but currently, steel sheets with extremely excellent corrosion resistance are mainly coated with an organic coating containing metallic zinc powder.
Steel plates that bake at 0°C are attracting attention. In particular, when electrogalvanized steel sheets made of alloys such as Zn-Ni, Zn-Ni-Cr, or Zn-Ni-Cr-Fe are used as the base for painted steel sheets, not only corrosion resistance but also press formability such as chipping resistance is improved. It will be a while ago.
しかしこのように鋼板製造時に焼付けという熱処理を施
すことは塗装焼付硬化性鋼板にとっては需要家にわたる
前に鋼板を硬化させてしまうことになり、需要家での成
形時に成形不良が発生し、もはや加工用素材としての価
値はない。このような意味から塗装焼付硬化性と高耐食
性を兼ね備えた表面処理鋼板の製造が要望されていたが
、未だかかる鋼板は製造されていないと言える。However, applying heat treatment called baking during the manufacturing of steel sheets in this way will harden the steel sheets before they reach the customer, which can lead to forming defects during forming at the customer, making it impossible to process them. It has no value as a material for use. From this point of view, there has been a demand for the production of surface-treated steel sheets that have both paint-baking hardenability and high corrosion resistance, but it can be said that such steel sheets have not yet been produced.
整して塗装焼付硬化能を付与するに十分な炭素を固溶体
として残存せしめ次鋼板に表面処理を施すに当って、鋼
板の調質圧延に特別の考慮を払い、塗装焼付硬化性をそ
こなうことなく高耐食性を有する表面処理鋼板を提供す
ることｔ目的とするものである・
本発明の要旨とするところは、ｃ：０．２０％以下、Ｍ
ｎ ： ２．０−以下、ｓｏｌ、Ａｔ： ０．１ ＯＳ
以下に加えて、必要に応じてＰ：０．１５０１以下、８
１０．８嘔以下、Ｂ：０．００５０チ以下のいずれか１
種もしくは２種以上を含み、残１！ＢＦ・および不可避
的不純物から成る鋼片を熱延および冷延によシ最終所望
板厚の鋼板とし、次いでこの鋼板ｋＡ０１〜９００℃に
加熱し、この温度範囲で５〜１８０秒保持したａ、１−
１０００ Ｖｓ＊ｅの平均冷却速贋で３００〜５００℃
に冷却し、この温度範囲に５〜６００秒保持−シ、シか
る後室温まで急冷し、次いで１．０チ以下の調質圧延を
施し、そのまま、もしくは電気亜鉛メッキ、もしくは亜
鉛を主とする電気複合メッキｉたは電気合金メッキを施
した抜、主として金属亜鉛粉末管含む有機系・皮膜を塗
装焼付し、′そのｆｏ、３〜１．５−〇調質圧延をｈす
こと１特徴とする塗装焼付硬化性を有する塗装鋼板の製
造方法にある。When applying the surface treatment to the steel plate, special consideration is given to the skin pass rolling of the steel plate, without impairing the bake hardenability of the steel plate. It is an object of the present invention to provide a surface-treated steel sheet having high corrosion resistance. The gist of the present invention is that c: 0.20% or less, M
n: 2.0- or less, sol, At: 0.1 OS
In addition to the following, P: 0.1501 or less, 8 as necessary
10.8 or less, B: 0.0050 or less
Contains a species or two or more species, only 1 left! A steel billet consisting of BF and unavoidable impurities was hot-rolled and cold-rolled into a steel plate having the final desired thickness, and then this steel plate was heated to kA01 to 900°C and held in this temperature range for 5 to 180 seconds. 1-
300-500℃ with an average cooling speed of 1000 Vs*e
After cooling to room temperature and holding it in this temperature range for 5 to 600 seconds, it is cooled rapidly to room temperature, then subjected to temper rolling of 1.0 inch or less, as it is, or electrogalvanized, or zinc-based. Electric composite plating or electroalloy plating is applied to the pipe, which is coated with an organic coating containing mainly metal zinc powder, and then subjected to temper rolling for 3~1.5-0 hours.1. The present invention provides a method for manufacturing a coated steel sheet having paint baking hardenability.
以下本発明における成分、製造条件の限定理由を詳述す
る。The reasons for limiting the components and manufacturing conditions in the present invention will be explained in detail below.
鋼板に塗装焼付硬化性を付与するには、鍋中にｃｔｍ溶
体どして残存せしめるととが必要であるが、固溶量が少
なすぎると通常Ｏ調質圧延程ｆ。In order to impart paint-baking hardenability to a steel plate, it is necessary to leave a CTM solution in the ladle, but if the amount of solid solution is too small, O temper rolling is usually required.
歪では歪時効が生ぜず、従って鋼板に塗装焼付硬化性を
付与することが出来ない、また、多過ぎると１食性塗装
鋼板製造時に時効硬化し、またＣ自身の固溶硬化によっ
て加工性の゛劣化が著しくなる。Strain does not cause strain aging, so it is not possible to impart paint-baking hardenability to the steel sheet.If the amount is too high, age hardening occurs during the production of monocorrosive coated steel sheets, and the solid solution hardening of C itself impairs workability. Deterioration becomes significant.
鋼板に塗装焼付硬化性を付与す為のに適量の固溶Ｃｆ：
残存せしめ゛るには、Ｃは０．２０優以下であることが
必要であ・る。鋼板の降伏強度を十分低くし、ランクフ
ォ＝ド′値管高めて加工性をより一層増すに二はＣ′ｔ
−０，０５−以下とすることが望ましい。Ｃの下限値と
しては通常０．０２−程度であるが、特に真空脱ガス処
理等によシｃ１１−ｏ、ｏｌ優以下とすることは、さら
に加工性を高めることになるので場合によって採用する
ことが望ましい。Appropriate amount of solid solute Cf to impart paint baking hardenability to the steel plate:
To ensure survival, C must be less than 0.20. The second thing to do is to lower the yield strength of the steel plate sufficiently, increase the Lanford's value, and further increase the workability.
It is desirable to set it to -0,05- or less. The lower limit of C is usually about 0.02-, but setting it to less than C11-o, OL, especially for vacuum degassing treatment, will further improve workability, so it may be adopted depending on the case. This is desirable.
Ｍｕは鋼の強靭化には有効な元素であるが゛、’ ２．
０−管超えると冷間加工性を低下させるため２．０％以
下とする。なお、フェライトとマルテンサイトの二相組
織鋼を得る場合を除き、Ｍｎはｌ、０チ以下が好ましい
。Mu is an effective element for toughening steel.'2.
If it exceeds 0-tube, cold workability will deteriorate, so the content should be 2.0% or less. Note that, except when obtaining a steel with a dual phase structure of ferrite and martensite, Mn is preferably 1,0 or less.
Ａｔは脱酸の目的で添加するが、その含有量がｔｅｌ、
ＡＡで０．１０Ｓ・を超えるとアル・主ナクラスターの
増加で表面性状を劣化させるので、−ｍｏｌ、Ａｔで０
．１０−以下とする。 ・ ・Ｐは固溶強化元
素として非常に有効であるが、その含有量が０．１５０
−超では鋼が着しく劣化するため、その添加量は０．１
５０％以下が好ましら、−一方、・Ｐを添加しない普通
鋼４−スの場合、伸びを確保する点からＰ量は０．０１
−以下が好ましい。 ・ ・
Ｓｌは安価に高強度特性が得られるのみならず本発明に
従ったＡＣ１〜９００℃の温度範囲の焼鈍の場合、その
温度域でフェライトとオーステナイトが均一に複合混在
し、その結果製品の強度と延性のバランスを向上させる
ので、フェライト・マルテンサイト二相鋼を主とした高
強度材を得る場合、 にはその添加が有効であるが、含
有量がｏ、 ｓ ｏ ｓを超えるとメッキ性を害するの
で、添加する場合はＯ，Ｓ Ｏｓ以内の添加が好ましい
・Ｂは少量の添加でＮを固定しＮによる時効を抑えるの
でｏ、ｏｏｓｏ＊以下の添加が好ましい。At is added for the purpose of deoxidation, but its content is tel,
If AA exceeds 0.10S, the surface quality will deteriorate due to an increase in Al/main clusters, so -mol, At will be 0.
．． 10- or less.・ ・P is very effective as a solid solution strengthening element, but its content is 0.150
- Since the steel deteriorates rapidly in ultra-high-grade steel, the amount added is 0.1
50% or less is preferable. On the other hand, in the case of ordinary steel without adding P, the P amount is 0.01 to ensure elongation.
-The following are preferred.・ ・ Sl can not only provide high strength properties at low cost, but also when annealing in the AC temperature range of 1 to 900°C according to the present invention, ferrite and austenite are mixed uniformly in that temperature range, and as a result, the product is Since it improves the balance between strength and ductility, its addition is effective when obtaining high-strength materials mainly made of ferrite-martensitic duplex steel, but if the content exceeds o, s o s, plating If B is added, it is preferably added in an amount within O, SO, since B impairs the properties of B. B is preferably added in an amount of O, ooso* or less, since a small amount of B fixes N and suppresses aging due to N.
次に本発明における処理条件について、その限定理由を
説明する。Next, the reasons for limiting the processing conditions in the present invention will be explained.
連続焼鈍における加熱速度は生産性を考慮して１１７ｓ
＠ｃ以上とすることが好ましい。次いで鋼板を再結晶温
度以上に保持するわけであるが、この保持温度が低すぎ
ると再結晶が起らないかおるいは起っても不十分であり
、また高すぎると結晶粒が粗大化し、プレス成形後の肌
荒れの原因となるため、保持温度の範囲をム。、〜９０
０℃とする。ｔた保持時間は５秒未満では再結晶が十分
でなく、１８０秒を超えると結晶粒が成長し過ぎて粗大
と表るため５〜１８０秒とする０次いでこの鋼板を冷却
してＣ會過飽和に固溶させた状態で過時効処理上行うが
、過時効源ｆまでの冷却速度が早すぎると焼きが入り硬
くカシすぎるとともに鋼板の形状がくずれるため１００
０ＶｌＣ以下とする。またこの冷却速度が遅すぎると、
過飽和度が小さくなシ過時効中の析出が抑えられ必要以
上に固溶Ｃが残存するためｌ Ｖａ＠ｃ以上とした。ま
た過時効源−は、３００℃未満では炭化物の十分な析出
が起こらず、５００℃を超えるとこの温度での平衡固溶
量まアは速やかに析出するものの平衡固溶量が多すぎ材
質を劣化させるので３００℃〜５００℃の範囲とする。The heating rate in continuous annealing is 117 seconds considering productivity.
It is preferable to set it as @c or more. Next, the steel plate is held at a temperature above the recrystallization temperature, but if this holding temperature is too low, recrystallization will not occur, or even if it does occur, it will be insufficient; if it is too high, the crystal grains will become coarse, This may cause rough skin after press molding, so please limit the holding temperature range. ,~90
The temperature shall be 0°C. If the holding time is less than 5 seconds, recrystallization will not be sufficient, and if it exceeds 180 seconds, the crystal grains will grow too much and appear coarse. However, if the cooling rate to the overaging source f is too fast, it will become hard and become too hard, and the shape of the steel sheet will collapse.
0VlC or less. Also, if this cooling rate is too slow,
Precipitation during sieving aging, where the supersaturation degree is small, is suppressed and more solid solution C remains than necessary, so it is set to l Va@c or more. In addition, the source of over-aging is that sufficient precipitation of carbides does not occur at temperatures below 300°C, and at temperatures above 500°C, although the equilibrium solid solution amount at this temperature quickly precipitates, the equilibrium solid solution amount is too large and the material deteriorates. Since it causes deterioration, the temperature is set in the range of 300°C to 500°C.
またこの温度範囲における保持時間は冷延鋼板としての
材質確保のために５秒以上６００秒以下とする。しかる
抜過時効温度から室温まで急冷して、所望の固溶Ｃ量と
する。Further, the holding time in this temperature range is set to 5 seconds or more and 600 seconds or less in order to ensure the quality of the material as a cold rolled steel sheet. It is rapidly cooled from the appropriate extraction aging temperature to room temperature to obtain a desired amount of solid solute C.
次いでかかる熱処理を施した鋼板に調質圧延をかけるが
、との調質圧延はこれに続くメッキ工程での鋼板の電極
への接触中腰折れを防止するために不可欠な工程である
が、その圧下率が１．０チを超えると、この段階での機
械的性質の劣化が大きく、またこれに続く耐食性皮膜鋳
付の工程での歪時効による材質の劣化も著しくなるため
１．−質圧延率は１．０ｓ以下、好ましくは０３〜０．
６チとする。The heat-treated steel plate is then subjected to temper rolling, which is an essential process to prevent the steel plate from bending during contact with the electrode in the subsequent plating process. If the ratio exceeds 1.0, the deterioration of mechanical properties at this stage will be significant, and the deterioration of the material due to strain aging in the subsequent process of casting the corrosion-resistant coating will also be significant.1. - The quality rolling rate is 1.0 s or less, preferably 0.3 to 0.0 s.
Let's say 6chi.
次いで、この鋼板をそのまま、本しくは電気亜鉛メッキ
、もしくは亜鉛を主とする電気複合メッキまたは電気合
金メッキを施して有機系被膜の塗装のための下地鋼板と
するわけであるが、耐食性、耐ハクリ性等のプレス性お
よび溶接性に優ねた塗装鋼板を得るには耐食性、プレス
性に優ねた亜鉛合金電気メッキを施すことが好ましいが
、中でも特に溶接性に優れたＺｎ −Ｎｉ −Ｃｒ −
Ｆｅ系の合金電気亜鉛メッキを施して下地鋼板とするこ
とが好ましい。さらに、有機系被膜には、溶液性の観点
から金属亜鉛粉末以外に１〜４０チのステンレス粉末を
含ませることは特に好ましい。また、有機系被膜の焼付
に除しては、近赤外又は赤外領域の熱沖ヲ用いて、２０
０〜３００℃で１０秒以内で焼付ける方法が、被膜鋳付
時の歪時効を抑え需要家での成形性を劣化させない点か
ら、特に好ましい。Next, this steel sheet is used as a base steel sheet for coating with an organic coating by electrolytic galvanizing, electrolytic composite plating or electroalloy plating mainly consisting of zinc, but corrosion resistance and resistance are In order to obtain coated steel sheets with excellent pressability such as peelability and weldability, it is preferable to apply zinc alloy electroplating, which has excellent corrosion resistance and pressability. −
It is preferable to electrogalvanize the Fe-based alloy to form the base steel sheet. Further, from the viewpoint of solution properties, it is particularly preferable that the organic coating contains 1 to 40 pieces of stainless steel powder in addition to metal zinc powder. In addition, for baking organic coatings, heat treatment in the near-infrared or infrared region is used to
A method of baking at 0 to 300° C. within 10 seconds is particularly preferable because it suppresses strain aging during coating casting and does not deteriorate moldability at the customer's end.
このような表面処理を施し次のちの鋼板に再び調質圧延
管施すが、との調質圧延は需を家での塗装焼付工程で歪
時効を生ぜしめるに十分な新しい転位を鋼板中に導入す
る目的で行うものであり、その圧下率は０．３参未満ア
は歪時効を生ぜしめるに十分な転位が導入されず、また
１、 ５チ超では加工硬化のために延性が劣化するので
０．３〜１．５％とした。降伏点上昇や伸び劣化を最小
限にするには０．６−以下の調圧が好ましい。After this surface treatment, the steel plate is then temper-rolled again, but the heat-rolling process introduces enough new dislocations into the steel plate to cause strain aging during the paint baking process at home. If the rolling reduction is less than 0.3 mm, sufficient dislocations will not be introduced to cause strain aging, and if it exceeds 1.5 mm, the ductility will deteriorate due to work hardening. The content was set at 0.3 to 1.5%. In order to minimize increase in yield point and deterioration in elongation, pressure adjustment of 0.6- or less is preferable.
このようにして製造された表面処理鋼板は耐食性、プレ
ス性、溶接性に優れることに加え、被膜焼付後も高い塗
装焼付硬化性を有するという、他の耐食性塗装鋼板と比
して大きな利点を有する・なお本発明での鋼片とは、通
常の方法で溶製された分塊スラブ又は鋳片を含み、鋳片
の熱延冷延条件にも制約はない・
以下本発明を実施例によシ具体的に説明する。The surface-treated steel sheets manufactured in this way have excellent corrosion resistance, pressability, and weldability, and also have high paint hardenability even after the coating has been baked, which is a major advantage over other corrosion-resistant coated steel sheets.・Note that the steel billet in the present invention includes a bloomed slab or slab produced by a normal method, and there are no restrictions on the hot-rolling and cold-rolling conditions for the billet. This will be explained in detail.
使用した鋼の成分を表１に示す。Table 1 shows the composition of the steel used.
に示すが、本例では１次冷却速度と過時効温度以外は、
焼鈍温度までの加熱速度１０１７ｓ＠ｃ 、再結晶焼鈍
７８０℃ｘ１分 ２次冷却は室温まで約２０００ Ｖｔ
＠ｅの冷却速度で急冷とした。表２に本例で用いた１次
冷却および過時効の条件を示す・焼鈍稜の調圧率は０．
５〜１．２−の間で変化させ九。However, in this example, except for the primary cooling rate and overaging temperature,
Heating rate up to annealing temperature: 1017 s@c, recrystallization annealing at 780°C x 1 minute, secondary cooling at about 2000 Vt to room temperature
Rapid cooling was performed at a cooling rate of @e. Table 2 shows the conditions of primary cooling and overaging used in this example.・The pressure adjustment rate of the annealing ridge was 0.
Vary between 5 and 1.2-9.
このような鋼板に、Ｚｎｔ−主成分とし、Ｎｌ’ｉ１３
重量−１Ｆ＠を３重量−１ＣＦを０．３重量％含む合金
ｔ２０１／ｍ”はど電気メッキした鋼板を用い、こＯメ
、中鋼板に３５重量−のステンレス粉末を含むジンクリ
、チ塗料を１０μの厚みで塗装し、焼付けた。焼付処理
サイクルを第２図に示す。In such a steel plate, Znt is the main component and Nl'i13
An alloy T201/m" containing 0.3% by weight of 0.3% by weight of 1F by weight was used, and a zinc chloride paint containing 35% by weight of stainless steel powder was applied to the medium steel plate. It was coated to a thickness of 10μ and baked.The baking treatment cycle is shown in Figure 2.
すなわち、本発明の効果を引き出す上で特に好ましいと
した近赤外領域の加熱源を用いて２５０℃で１０秒以内
で焼付処理を行ったもので、２５０℃までの加熱速度５
０ Ｖｍ＠ａ 、 ２８０℃に到達後直ちに５ＯＶ−・
Ｃの冷却速度で室温まで急冷した。That is, the baking process was performed at 250°C within 10 seconds using a heating source in the near-infrared region, which is particularly preferable for bringing out the effects of the present invention, and the heating rate up to 250°C was 5.
0 Vm@a, 5OV-・immediately after reaching 280℃
The mixture was rapidly cooled to room temperature at a cooling rate of C.
被膜焼付抜の調質圧延率は０．５〜２．０％の間で変化
させた・
このようにして製造した表面処理鋼板の耐食性の評価に
は、ＪＩＳＺ２３７１で規定された塩水噴霧試験の促進
法と考えられるサイクル腐食試験を用いたが、その条件
ｔ−表３に示す。The temper rolling ratio for removing the film burn-out was varied between 0.5 and 2.0%. To evaluate the corrosion resistance of the surface-treated steel sheets produced in this way, accelerated salt spray testing as specified in JIS Z2371 was used. A cyclic corrosion test, which is considered to be a method, was used, and its conditions are shown in Table 3.
表３ サイクル腐食試験条件
また、ス／、）溶接性は連続溶接２０００打点以上での
ナゲツト径の変化を評価基準とした。Table 3 Cyclic Corrosion Test Conditions Weldability was evaluated based on the change in nugget diameter at 2000 continuous welding points or more.
表４に評価結果を示す。Table 4 shows the evaluation results.
１ｉ！４から本発明材の優位性は明らかである。すなわ
ち、有機系被膜焼付後調質圧延を行わなかったもの（Ａ
ｌ ３ ）では鋼板が歪時効によシ硬化するとともに降
伏点伸びが著しく回復しておシ、被膜焼付処理前彼の調
質圧延率が本発明の範囲よシ高めに外れているもの（Ａ
４ 、５ 、６ 、１０ ）ではいずれ４加工硬化によ
り降伏点、伸びが本発明材と比べ著しく悪くなっている
。また箱焼鈍を行ったもの（雇ｌ）では塗装焼付硬化性
がほとんどなく、１次冷速か本発明の範囲よシ高目に外
れているもの（Ｉ６７）は降伏点、伸びの劣化が大きく
、また、過時効温度が本発明の範囲よシ高めに外れてい
るもの（Ａｌ ２ ’）および低めに外れているもの（
Ａ８）ではいずれも固溶ＣＯ析出が不十分でＴｏシ時効
による降伏点伸びが発生している。1i! 4, the superiority of the material of the present invention is clear. That is, those in which temper rolling was not performed after baking the organic coating (A
In the case of 3), the yield point elongation significantly recovered as the steel plate hardened through strain aging, and the temper rolling rate before the coating baking treatment was much higher than the range of the present invention (A).
4, 5, 6, and 10), the yield point and elongation became significantly worse due to work hardening than the materials of the present invention. In addition, those subjected to box annealing (I67) have almost no paint baking hardenability, and those whose primary cooling rate is outside the range of the present invention (I67) have a large deterioration in yield point and elongation. , and those whose overaging temperature is higher than the range of the present invention (Al 2 ') and those whose overaging temperature is lower than the range of the present invention (Al2').
In all cases of A8), precipitation of solid solution CO was insufficient and yield point elongation occurred due to Toshiba aging.
本発明材は機械的性質、耐食性、溶接性ともに優れてお
り、自動車部品のうちプレス加工が厳しく、かつ耐食性
も要求される部品に有効に使用される効果があることは
明らかである。It is clear that the material of the present invention has excellent mechanical properties, corrosion resistance, and weldability, and can be effectively used in automobile parts that require severe press processing and also require corrosion resistance.
第１図は本発明実施例の焼鈍サイクル１表わし、第２９
社本発明実施例の有機系被膜の焼付処理サイクルを表わ
す。
特許出願人 新日本製鐵株式會社FIG. 1 shows the annealing cycle 1 of the embodiment of the present invention, and the 29th
2 shows a baking treatment cycle for an organic coating according to an embodiment of the present invention. Patent applicant Nippon Steel Corporation
Claims (1)
ｍｏｌ、ＡＡ：ｏ、１０１以下に加工”ｃ、必要に応じ
？ Ｐ ：０．１５０チ以下、ｓｔ：ｏ、ｓ＊以下、Ｂ
：０．００５０Ｓ以下のいずれか１種もしくは２種以上
を含み、残１１Ｆ・および不可避的不純物からなる鋼片
を熱嬌および冷延によシ最終所望板厚の鋼板とＬ７、次
いでこの鋼板を、ＡＣ１〜９００℃に加熱し、この温度
範囲で５〜１８０秒保持した後、ｌ〜１０００℃／８＠
１１の平均冷却速度で３００〜５００℃に冷却し、この
温度範囲に５〜６００秒保持し、しかる後室温まで急冷
し、次いで１．０ｑＩＩ以下の調質圧延を施し、そのま
ま、もしくは電気亜鉛メッキ、もしくは亜鉛金主とする
電気複合メッキまたは電気合金メ。 キを施し九後、主として金属亜鉛粉末を含む有機系被膜
を塗装焼付し、その後０．３〜ｔ、ＳＳＯ調質圧延を施
すことを特徴とする塗装焼付硬化性を有する塗装鋼板Ｏ
ａＶ造方法。[Claims] C20.20'11 or less, Mu22.0% or less,
mol, AA: o, processed to 101 or less"c, if necessary? P: 0.150 or less, st: o, s* or less, B
: A steel piece containing one or more of the following: 0.0050S or less, remaining 11F and unavoidable impurities is hot-rolled and cold-rolled to form a steel plate of the final desired thickness and L7, and then this steel plate is , after heating to AC1~900℃ and holding in this temperature range for 5~180 seconds, l~1000℃/8@
Cooled to 300 to 500 °C at an average cooling rate of 11, held in this temperature range for 5 to 600 seconds, then rapidly cooled to room temperature, and then subjected to temper rolling of 1.0 qII or less, and either as is or electrogalvanized. or zinc-gold-based electrocomposite plating or electroalloy metal. A coated steel sheet O having paint-baking hardenability, characterized in that after the coating, an organic coating mainly containing metallic zinc powder is painted and baked, and then SSO temper rolling is applied for 0.3 to 1000 t.
aV construction method.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP14498781A JPH0232326B2 (en) | 1981-09-14 | 1981-09-14 | TOSOYAKITSUKEKOKASEIOJUSURUTOSOKOHANNOSEIZOHOHO |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP14498781A JPH0232326B2 (en) | 1981-09-14 | 1981-09-14 | TOSOYAKITSUKEKOKASEIOJUSURUTOSOKOHANNOSEIZOHOHO |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS5845322A true JPS5845322A (en) | 1983-03-16 |
| JPH0232326B2 JPH0232326B2 (en) | 1990-07-19 |
Family
ID=15374836
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP14498781A Expired - Lifetime JPH0232326B2 (en) | 1981-09-14 | 1981-09-14 | TOSOYAKITSUKEKOKASEIOJUSURUTOSOKOHANNOSEIZOHOHO |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH0232326B2 (en) |
Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS63241122A (en) * | 1987-03-28 | 1988-10-06 | Sumitomo Metal Ind Ltd | Production of hot dip zinc coated steel sheet for ultra-deep drawing |
| JPH07242948A (en) * | 1994-02-28 | 1995-09-19 | Kobe Steel Ltd | Production of cold rolled steel sheet for deep drawing excellent in baking hardenability |
| JP2002295736A (en) * | 2001-03-29 | 2002-10-09 | Kawasaki Steel Corp | Method for manufacturing coated steel pipe |
| JP2007327104A (en) * | 2006-06-08 | 2007-12-20 | Nisshin Steel Co Ltd | Manufacturing method of coated steel sheet with excellent surface appearance |
| JP2015520296A (en) * | 2012-04-11 | 2015-07-16 | タタ、スティール、アイモイデン、ベスローテン、フェンノートシャップＴａｔａ Ｓｔｅｅｌ Ｉｊｍｕｉｄｅｎ Ｂｖ | Polymer coated substrate for packaging applications and method for producing the coated substrate |
-
1981
- 1981-09-14 JP JP14498781A patent/JPH0232326B2/en not_active Expired - Lifetime
Cited By (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS63241122A (en) * | 1987-03-28 | 1988-10-06 | Sumitomo Metal Ind Ltd | Production of hot dip zinc coated steel sheet for ultra-deep drawing |
| JPH0699760B2 (en) * | 1987-03-28 | 1994-12-07 | 住友金属工業株式会社 | Method for producing steel plate with hot dip zinc for ultra deep drawing |
| JPH07242948A (en) * | 1994-02-28 | 1995-09-19 | Kobe Steel Ltd | Production of cold rolled steel sheet for deep drawing excellent in baking hardenability |
| JP2002295736A (en) * | 2001-03-29 | 2002-10-09 | Kawasaki Steel Corp | Method for manufacturing coated steel pipe |
| JP4631193B2 (en) * | 2001-03-29 | 2011-02-16 | Ｊｆｅスチール株式会社 | Method for producing coated steel pipe |
| JP2007327104A (en) * | 2006-06-08 | 2007-12-20 | Nisshin Steel Co Ltd | Manufacturing method of coated steel sheet with excellent surface appearance |
| JP2015520296A (en) * | 2012-04-11 | 2015-07-16 | タタ、スティール、アイモイデン、ベスローテン、フェンノートシャップＴａｔａ Ｓｔｅｅｌ Ｉｊｍｕｉｄｅｎ Ｂｖ | Polymer coated substrate for packaging applications and method for producing the coated substrate |
Also Published As
| Publication number | Publication date |
|---|---|
| JPH0232326B2 (en) | 1990-07-19 |
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