JPH0358595B2 - - Google Patents
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- Publication number
- JPH0358595B2 JPH0358595B2 JP61000272A JP27286A JPH0358595B2 JP H0358595 B2 JPH0358595 B2 JP H0358595B2 JP 61000272 A JP61000272 A JP 61000272A JP 27286 A JP27286 A JP 27286A JP H0358595 B2 JPH0358595 B2 JP H0358595B2
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- Prior art keywords
- steel
- corrosion resistance
- less
- workability
- layer
- Prior art date
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Description
（産業上の利用分野）
本発明は優れた加工性と耐食性を有するステン
レスクラツド鋼板に関するものである。
（従来の技術）
自動車、家庭電器製品に使用される鋼板に代表
されるように、鋼板はプレス加工後、リン酸塩処
理（化成処理）をし、塗装を行つて耐食性が付与
される。従来、深絞り性の優れた冷延鋼板とし
て、低脱Alキルド鋼板が使用されて来た。これ
らの鋼板では塗装によつて耐食性が付与される
が、耐食耐久性が十分でなかつた。
一方、耐食性の点ではオーステナイト系ステン
レス鋼板が最も優れているが、コストが普通鋼に
比べ著しく高い。このため、コストが低く耐食性
が優れている鋼板として、従来からステンレスク
ラツド鋼板が開発されて来た。
普通鋼とステンレスのクラツド鋼板では、Cr
とＣの親和性が高く、普通鋼層からステンレス鋼
層へのＣの拡散が起こり、耐食性が低下する問題
があつた。これを防止するため普通鋼側に炭化物
形成元素を添加して、Ｃの拡散を防止する技術が
開示されている（特公昭58−15310号公報、特公
昭58−19381号公報、米国特許第3693242号公報）。
しかし、これらの開示技術ではＣ，Ｎ量が多
く、かつ、Ti，Nb量も多く使用するため十分な
加工性が得られず、コストも高い。また、Ｃの拡
散を防止する別の方法として、界面層にNiメツ
キしたり、Ni箔を挿入する方法も提案されてい
るが、コストが著しく高くなる問題があつた。
かつまた、製造方法もサンドイツチ状に溶接組
立後熱間圧着する方法にのみ依存しているため、
歩留が低くコストが高かつた。
本発明者らはすでに、少なくとも片側表層部に
2.5〜15％のオーステナイトステンレス層を有す
るクラツド鋼板を発明した。
（発明が解決しようとする問題点）
本発明は、電磁加熱性、耐食性、加工性、経済
性に優れたオーステナイト系ステンレスクラツド
鋼板を提供するものである。
（問題点を解決するための手段）
本発明は内層が極低炭素鋼、両表層がオーステ
ナイト系ステンレス鋼からなる３層ステンレスク
ラツド鋼板の提供にあり、その要旨とするところ
は、Ｃ≦0.0045％，Al≦0.080％，Mn≦1.0％，Ｎ
≦0.0050％およびTi，Nbのうち１種又は２種を
含む極低炭素鋼板において、（Ti＋Nb）量が0.15
％以下で、かつ下記１式を満足する内層部と
Nb／7.74C＋Ti／4C＋3.43N≧0.8 …１式
オーステナイト系ステンレス鋼からなる表層部
を少くとも片面に持つ加工性および耐食性の優れ
たステンレスクラツド鋼板である。
以下、本発明を詳細に説明する。
まず本発明鋼板における内層のＣ，Al，Ｎ，
Mnの限定理由について述べる。
Ｃは0.0045％を超えると延性が低下するばかり
でなく、優れた深絞り性を確保するための（Ti
＋Nb）量を多くする必要がある。また、Ｃが
0.0045％を超えると、内層と表層の境界面にクロ
ム炭化物が析出しやすくなり、耐食性の点から好
ましくない。
Ｃ量は少ない方が良いが、製鋼での溶製コスト
の点から、自ずと下限が決まるので特に限定しな
いが、コストの点から10ppm未満にすることは得
策でなく、好ましい範囲は0.0010〜0.0040％であ
る。
Alは脱酸のためおよびNb，Tiの添加による時
効性・加工性向上効果を最大限に発揮するため
に、0.005％以上必要であるが、0.08％超では効
果が飽和しコストも上昇する。好ましい範囲は
0.015〜0.060％である。
ＮはNb，Tiの加工性向上効果を減ずるので
50ppm以下とするが、40ppm以下可及的に少なく
することが、加工性の点から好ましい。しかし現
状の製鋼技術から見て、5ppm未満とすることは
コストの点から得策ではない。
Mnは1.0％を超えると強度が増加し、加工性が
低下するので1.0％以下とする。高い強度を意図
しない場合は、優れた加工性を確保する点から、
0.50％以下とすることが好ましく、0.35％以下に
することによつて、最高度の加工性が発揮され
る。また下限については、優れた熱間加工性を確
するため0.05％以上とすることが好ましい。
次に、本発明では内層部にTi，Nbを添加して
いるが、内層部のTi，Nb量は、優れた加工性と
時効による加工性劣化を防ぐため、および内層か
ら表層のステンレス部へのＣの拡散を抑えるた
め、Ｃ，Ｎ量の限定に加えて、１式、すなわち
Ｃ，Ｎとの化学当量比を0.8以上とする必要があ
る。
Nb／7.74C＋Ti／4C＋3.43N≧0.8 …１
（ここでNb，Ti，Ｃ，Ｎは各元素の重量％）
この化学当量比を1.0以上にすることによつて、
本発明の効果は最大限に発揮される。表層にはオ
ーステナイト系ステンレスを用いるが、その成分
はJIS Ｇ 4303に規制される成分範囲であればよ
い。例えば、SUS 304では、Ｃ量は0.08％以下で
あるが、Ｃ量を0.05％以下にすることによつて、
ホツトコイル焼鈍を省略できる効果がある。
本発明のステンレスクラツド鋼板は、好ましく
は表層部の厚みを片面で、製品クラツド率として
2.5％〜30％にする。クラツド率が2.5％以下にな
ると、表層のSUS層が破れて内層が露出しやす
く、耐食性が損なわれるので、表層のSUS層の
下限を片側2.5％以上、両側で５％以上とする。
また、クラツド率が片側30％超、両側で60％超
になると、クラツド化によるコストメリツトが少
なくなるので、クラツド率の上限は片側30％以下
（両側60％以下）とする。
本発明のクラツド鋼板の製造方法は普通鋼への
SUS肉盛を鋳込法により行うことがコストの点
から望ましい。この１例を次に説明する。
普通鋼スラブを芯材とし、これを垂直に直立さ
せる。このスラブ周囲にモールドを配し、モール
ド上部には耐火枠を配置する。この耐火枠の外周
には、高周波加熱コイルを設置し、耐火枠中に流
入せしめたSUS溶湯を加熱し、スラブ外周に
SUSを肉盛する。
このとき内層となる普通鋼のスラブ表面にはフ
ラツクスを塗布し、酸化を防止しつつ700〜1000
℃に予熱し、界面の溶着を完全にする。この他、
例えば圧延圧着でも、本発明方法ではNi箔を表
層〜内層境界にもう入する必要がなく、低コスト
化の優れた効果を有している。
得られたスラブは通常行なわれるように熱間圧
延される。熱延鋼板として使用される場合は、
900℃以上の焼鈍を施して、熱間圧延時の歪を解
放することが加工性の点から好ましい。冷延鋼板
とする場合は、通常行なわれるように、かつ熱延
コイルを焼鈍後、10％以上（好ましくは30％以
上）の冷間圧延をし、表層部の再結晶温度以上か
つ1100℃以下の温度で焼鈍する。
なお表層ステンレスのＣ量を、0.05％以下（好
ましくは0.04％以下）に特定し、かつ本内層成分
と組合わせ、熱延時巻き取り温度を600℃以下の
場合は、熱延コイルの焼鈍を省略しても、酸洗時
に粒界腐色を生ずることもないので、熱延コイル
の焼鈍省略が可能となる。
さらに表層部のＣが0.05％以下（好ましくは
0.04％以下）の場合には、冷延後の焼鈍温度を
900〜950℃までに低減しても、優れた耐食性が維
持出来、優れた深絞り性も発揮できるので、表層
ステンレスのＣ≦0.05％とすることによつて、本
発明の効果は一層向上する。
第１図はC0.04％，Si0.02％，Mn0.3％，
N0.0025％，Al0.050％の内層と、SUS304の表層
からなる３層ステンレスクラツド鋼(A)と、本発明
成分（C0.0035％，Si0.02％，Mn0.3％，N0.0030
％，Al0.036％，Ti0.07％の内層と、SUS304の表
層からなる本発明鋼(B)を、仕上温度910℃で４mm
に熱延後、板厚0.5〜0.8mmに冷延後、1100℃で焼
鈍したクラツド率０〜60％の３層ステンレスクラ
ツド鋼板の強度〜延性バランスを示す。
本発明鋼(A)は比較鋼(B)に比べ、同一引張強さで
比較して高い延性が得られる。
（実施例）
第１表は本発明および比較のステンレスクラツ
ド鋼の内層および表層の成分および各クラツド率
を示す。
この鋼板は先述の鋳込法で、本発明の250mm厚
クラツドスラブを製造し、4.0mmに熱延し、600℃
で巻き取つた。この後1100℃で焼鈍し（Ａ，Ｂ−
１，Ｃ−１，Ｄ−１）た。本発明成分鋼（Ｂ，
Ｃ）の一部は、熱延後の焼鈍を行なわなかつた
（Ｂ−２，Ｃ−２，Ｄ−２）。その後0.8mmに冷延
し、1100℃で焼鈍した。
この鋼板の引張試験値と耐食性を第２表に示
す。本発明鋼は比較クラツド鋼より引張強さに比
し高い延性を示す。
(Field of Industrial Application) The present invention relates to a stainless clad steel sheet having excellent workability and corrosion resistance. (Prior Art) Steel plates, as typified by steel plates used in automobiles and home appliances, are subjected to phosphate treatment (chemical conversion treatment) after press working, and are then painted to impart corrosion resistance. Conventionally, low-aluminum-free killed steel sheets have been used as cold-rolled steel sheets with excellent deep drawability. Although corrosion resistance is imparted to these steel plates by painting, the corrosion resistance durability was not sufficient. On the other hand, austenitic stainless steel sheets have the best corrosion resistance, but are significantly more expensive than ordinary steel. For this reason, stainless clad steel sheets have been developed as steel sheets that are low in cost and have excellent corrosion resistance. For ordinary steel and stainless steel clad steel sheets, Cr
There was a problem that C had a high affinity with C, and diffusion of C from the ordinary steel layer to the stainless steel layer occurred, resulting in a decrease in corrosion resistance. In order to prevent this, a technique has been disclosed in which a carbide-forming element is added to the ordinary steel to prevent the diffusion of C (Japanese Patent Publication No. 15310/1981, Japanese Patent Publication No. 19381/1981, U.S. Patent No. 3693242). Publication No.). However, these disclosed techniques use large amounts of C and N, as well as large amounts of Ti and Nb, so that sufficient workability cannot be obtained and the cost is high. Furthermore, as another method for preventing the diffusion of C, methods have been proposed in which the interface layer is plated with Ni or Ni foil is inserted, but these methods have the problem of significantly increasing costs. Moreover, the manufacturing method relies only on the method of welding and assembling into a sandwich shape and then hot-pressing.
The yield was low and the cost was high. The present inventors have already demonstrated that at least one surface layer
Invented a clad steel plate with a 2.5-15% austenitic stainless steel layer. (Problems to be Solved by the Invention) The present invention provides an austenitic stainless clad steel sheet having excellent electromagnetic heating properties, corrosion resistance, workability, and economic efficiency. (Means for Solving the Problems) The present invention provides a three-layer stainless clad steel sheet whose inner layer is made of ultra-low carbon steel and both surface layers are made of austenitic stainless steel, and its gist is that C≦0.0045 %, Al≦0.080%, Mn≦1.0%, N
In ultra-low carbon steel sheets containing ≦0.0050% and one or two of Ti and Nb, the amount of (Ti + Nb) is 0.15
% or less and an inner layer that satisfies the following formula 1: Nb/7.74C+Ti/4C+3.43N≧0.8...1 formula A stainless steel plate with excellent workability and corrosion resistance that has a surface layer made of austenitic stainless steel on at least one side. It is a steel plate. The present invention will be explained in detail below. First, the inner layer C, Al, N,
The reason for limiting Mn will be explained. When C exceeds 0.0045%, not only does ductility decrease, but also (Ti) is added to ensure excellent deep drawability.
+Nb) amount needs to be increased. Also, C
If it exceeds 0.0045%, chromium carbide tends to precipitate at the interface between the inner layer and the surface layer, which is unfavorable from the viewpoint of corrosion resistance. Although it is better to have a smaller amount of C, there is no particular limitation as the lower limit is naturally determined from the point of view of melting costs in steelmaking, but it is not a good idea to make it less than 10 ppm from the point of view of cost, and the preferable range is 0.0010 to 0.0040%. It is. Al is required in an amount of 0.005% or more for deoxidation and to maximize the effects of improving aging and workability due to the addition of Nb and Ti, but if it exceeds 0.08%, the effect will be saturated and the cost will increase. The preferred range is
It is 0.015-0.060%. Since N reduces the workability improvement effect of Nb and Ti,
The content should be 50 ppm or less, but preferably 40 ppm or less as much as possible from the viewpoint of processability. However, considering the current steel manufacturing technology, it is not a good idea to reduce the content to less than 5 ppm from the viewpoint of cost. If Mn exceeds 1.0%, the strength will increase and the workability will decrease, so it should be kept at 1.0% or less. If high strength is not intended, from the viewpoint of ensuring excellent workability,
It is preferable to set it to 0.50% or less, and the highest degree of workability is exhibited by setting it to 0.35% or less. Furthermore, the lower limit is preferably 0.05% or more in order to ensure excellent hot workability. Next, in the present invention, Ti and Nb are added to the inner layer, but the amount of Ti and Nb in the inner layer is determined to ensure excellent workability and prevent deterioration of workability due to aging, and from the inner layer to the surface stainless steel part. In order to suppress the diffusion of C, in addition to limiting the amounts of C and N, it is necessary to set one formula, that is, the chemical equivalence ratio with C and N to 0.8 or more. Nb/7.74C+Ti/4C+3.43N≧0.8...1 (Here, Nb, Ti, C, and N are weight% of each element) By setting this chemical equivalence ratio to 1.0 or more,
The effects of the present invention are maximized. Austenitic stainless steel is used for the surface layer, but its components may be within the range regulated by JIS G 4303. For example, in SUS 304, the C content is 0.08% or less, but by reducing the C content to 0.05% or less,
This has the effect of omitting hot coil annealing. The stainless clad steel sheet of the present invention preferably has a thickness of the surface layer on one side and a product cladding ratio of
Set it to 2.5% to 30%. When the cladding ratio is less than 2.5%, the surface SUS layer is likely to tear and the inner layer is exposed, impairing corrosion resistance. Therefore, the lower limit of the surface SUS layer is set to 2.5% or more on one side and 5% or more on both sides. Furthermore, if the cladding rate exceeds 30% on one side and 60% on both sides, the cost benefit of cladding will decrease, so the upper limit of the cladding rate should be 30% or less on one side (60% or less on both sides). The method for producing clad steel sheets of the present invention is a method for producing clad steel sheets.
From the viewpoint of cost, it is desirable to perform SUS overlaying by the casting method. An example of this will be explained next. A common steel slab is used as the core material and is stood vertically. A mold is placed around this slab, and a refractory frame is placed above the mold. A high-frequency heating coil is installed around the outer periphery of this refractory frame to heat the molten SUS metal that has flowed into the refractory frame.
Overlay SUS. At this time, flux is applied to the surface of the ordinary steel slab that will serve as the inner layer, and a flux of 700 to 1000 is applied to prevent oxidation.
Preheat to ℃ to ensure complete welding of the interface. In addition,
For example, even in rolling crimping, the method of the present invention does not require the addition of Ni foil at the boundary between the surface layer and the inner layer, and has an excellent cost reduction effect. The resulting slab is hot rolled in the usual manner. When used as hot rolled steel sheet,
From the viewpoint of workability, it is preferable to perform annealing at 900°C or higher to release strain during hot rolling. In the case of cold-rolled steel sheets, after annealing the hot-rolled coil, it is cold-rolled by 10% or more (preferably 30% or more) as usual, and the temperature is above the recrystallization temperature of the surface layer and below 1100℃. Anneal at a temperature of In addition, if the C content of the surface stainless steel is specified to be 0.05% or less (preferably 0.04% or less), combined with the main inner layer components, and the winding temperature during hot rolling is 600℃ or less, annealing of the hot rolled coil is omitted. However, since grain boundary corrosion does not occur during pickling, annealing of the hot-rolled coil can be omitted. Furthermore, the C content in the surface layer is 0.05% or less (preferably
0.04% or less), the annealing temperature after cold rolling should be
Even if the temperature is reduced to 900-950°C, excellent corrosion resistance can be maintained and excellent deep drawability can be exhibited, so the effect of the present invention is further improved by setting C≦0.05% in the surface stainless steel. . Figure 1 shows C0.04%, Si0.02%, Mn0.3%,
Three-layer stainless clad steel (A) consisting of an inner layer of N0.0025%, Al0.050%, and a surface layer of SUS304, and the ingredients of the present invention (C0.0035%, Si0.02%, Mn0.3%, N0. 0030
%, Al0.036%, Ti0.07% inner layer and SUS304 surface layer, 4mm thick at finishing temperature 910℃.
The figure shows the strength-ductility balance of a three-layer stainless steel clad steel sheet with a cladding ratio of 0 to 60%, which was hot rolled to a thickness of 0.5 to 0.8 mm, then annealed at 1100°C. The steel of the present invention (A) has higher ductility than the comparative steel (B) at the same tensile strength. (Example) Table 1 shows the components of the inner layer and surface layer of the stainless clad steels of the present invention and comparative stainless steels, and the clad ratios of each. This steel plate was produced by manufacturing the 250 mm thick clad slab of the present invention using the above-mentioned casting method, hot rolling it to 4.0 mm, and heating it at 600°C.
I rolled it up. After that, it was annealed at 1100℃ (A, B-
1, C-1, D-1). The composition steel of the present invention (B,
Some of C) were not annealed after hot rolling (B-2, C-2, D-2). It was then cold rolled to 0.8 mm and annealed at 1100°C. Table 2 shows the tensile test values and corrosion resistance of this steel plate. The inventive steel exhibits higher ductility relative to tensile strength than the comparative clad steel.
【表】【table】
【表】
（発明の効果）
本発明は以上詳述したように、加工性・耐食性
の優れたステンレスクラツド鋼を提供するもの
で、その経済的効果は大きい。[Table] (Effects of the Invention) As detailed above, the present invention provides a stainless clad steel with excellent workability and corrosion resistance, and its economic effects are significant.
第１図は本発明鋼と比較鋼の引張強さと延性
（全伸び）の関係を示す図表である。
FIG. 1 is a chart showing the relationship between tensile strength and ductility (total elongation) of the steel of the present invention and comparative steel.
Claims (1)
≦0.0050％およびTi，Nbのうち１種又は２種を
含む極低炭素鋼板において、（Ti＋Nb）量が0.15
％以下で、かつ下記１式を満足する内層部と Nb／7.74C＋Ti／4C＋3.43N≧0.8 …１式 オーステナイト系ステレンス鋼からなる表層部
を少くとも片面にもつことを特徴とする加工性お
よび耐食性の優れたステンレスクラツド鋼板。 ２ 表層部の厚みを片面で、クラツド率2.5％−
30％としたことを特徴とする特許請求の範囲第１
項記載の加工性および耐食性の優れたステンレス
クラツド鋼板。[Claims] 1 C≦0.0045%, Nn≦1.0%, Al≦0.080%, N
In ultra-low carbon steel sheets containing ≦0.0050% and one or two of Ti and Nb, the amount of (Ti + Nb) is 0.15
% or less and satisfying the following formula 1 and the surface layer made of Nb/7.74C+Ti/4C+3.43N≧0.8...1 formula austenitic stainless steel on at least one side.Workability and corrosion resistance. Superior stainless steel plate. 2 Surface layer thickness on one side, cladding rate 2.5% -
Claim 1 characterized in that the percentage is 30%.
Stainless clad steel sheet with excellent workability and corrosion resistance as described in Section 1.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| US07/150,496 US4861682A (en) | 1985-05-29 | 1988-02-01 | Clad steel materials having excellent ductility and corrosion resistance |
Applications Claiming Priority (2)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP60-114327 | 1985-05-29 | ||
| JP11432785 | 1985-05-29 |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS6259034A JPS6259034A (en) | 1987-03-14 |
| JPH0358595B2 true JPH0358595B2 (en) | 1991-09-05 |
Family
ID=14635046
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP27286A Granted JPS6259034A (en) | 1985-05-29 | 1986-01-07 | Stainless clad steel plate having excellent workability and corrosion resistance |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS6259034A (en) |
Families Citing this family (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS6369942A (en) * | 1986-09-10 | 1988-03-30 | Nippon Steel Corp | Stainless steel-clad metal sheet having superior workability and corrosion resistance |
| US5370946A (en) * | 1993-03-31 | 1994-12-06 | Allegheny Ludlum Corporation | Stainless steel and carbon steel composite |
| KR100438918B1 (en) * | 2001-12-08 | 2004-07-03 | 엘지전자 주식회사 | Method and apparatus for driving plasma display panel |
| CN110499453B (en) * | 2018-05-16 | 2021-09-17 | 宝山钢铁股份有限公司 | High-strength double-sided stainless steel composite board and manufacturing method thereof |
Family Cites Families (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS6030294B2 (en) * | 1978-09-26 | 1985-07-16 | 株式会社ミドリ十字 | Method for heat treatment of fractions containing glycoproteins that promote differentiation and proliferation of human granulocytes |
| JPS6043465A (en) * | 1983-08-19 | 1985-03-08 | Nippon Kokan Kk <Nkk> | Hot-rolled clad steel sheet with excellent low-temperature toughness and its manufacturing method |
-
1986
- 1986-01-07 JP JP27286A patent/JPS6259034A/en active Granted
Also Published As
| Publication number | Publication date |
|---|---|
| JPS6259034A (en) | 1987-03-14 |
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