JPH07185839A - Production of high-al-content ferritic stainless steel foil - Google Patents
Production of high-al-content ferritic stainless steel foilInfo
- Publication number
- JPH07185839A JPH07185839A JP34924393A JP34924393A JPH07185839A JP H07185839 A JPH07185839 A JP H07185839A JP 34924393 A JP34924393 A JP 34924393A JP 34924393 A JP34924393 A JP 34924393A JP H07185839 A JPH07185839 A JP H07185839A
- Authority
- JP
- Japan
- Prior art keywords
- foil
- stainless steel
- ferritic stainless
- clad
- heat treatment
- 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
Landscapes
- Pressure Welding/Diffusion-Bonding (AREA)
- Laminated Bodies (AREA)
- Solid-Phase Diffusion Into Metallic Material Surfaces (AREA)
Abstract
Description
【０００１】[0001]
【産業上の利用分野】本発明は、Ａｌ含有量の高いフェ
ライトステンレス鋼箔の製造方法に関する。特には、Ａ
ｌ含有量分布の均一性に優れ、かつ板厚変動が小さく、
優れた耐高温酸化性と電熱性を有するフェライトステン
レス鋼箔の製造方法に関する。本発明の製造方法により
得られるフェライトステンレス鋼箔は、発熱体や自動車
排ガス浄化装置の触媒担体などの材料に好適である。FIELD OF THE INVENTION The present invention relates to a method for producing a ferritic stainless steel foil having a high Al content. In particular, A
l Uniformity of content distribution is excellent, and plate thickness variation is small,
The present invention relates to a method for producing a ferritic stainless steel foil having excellent high temperature oxidation resistance and electric heat resistance. The ferritic stainless steel foil obtained by the production method of the present invention is suitable for materials such as a heating element and a catalyst carrier of an automobile exhaust gas purification apparatus.
【０００２】[0002]
【従来の技術】Ｃｒを多量に含有するフェライト系ステ
ンレス鋼板は、耐酸化性や耐食性に優れるので、この特
徴を生かして各種産業分野にて広範囲に使用されてい
る。フェライトステンレス鋼に一層の耐酸化性を付与す
るには、鋼中にＡｌを添加するのが有効である。しか
し、多量のＡｌの添加によって材質が非常に脆くなるた
め、冷間圧延はもちろんのこと熱間圧延さえも難しくな
る。このため、通常の圧延と焼鈍の組み合わせによって
高Ａｌステンレス鋼板を製造することは極めて困難であ
る。このような製造の困難性のため、高Ａｌフェライト
ステンレス鋼板は電気抵抗が高く、耐酸化性、耐食性に
優れた材料であるにもかかわらず、充分利用されるに至
っていない。2. Description of the Related Art Ferritic stainless steel sheets containing a large amount of Cr are excellent in oxidation resistance and corrosion resistance, and are widely used in various industrial fields by taking advantage of these characteristics. In order to impart further oxidation resistance to ferritic stainless steel, it is effective to add Al to the steel. However, the addition of a large amount of Al makes the material very brittle, so that not only cold rolling but also hot rolling becomes difficult. Therefore, it is extremely difficult to manufacture a high Al stainless steel sheet by a combination of ordinary rolling and annealing. Due to such difficulty of production, the high Al ferritic stainless steel sheet has not been used sufficiently even though it is a material having high electric resistance and excellent oxidation resistance and corrosion resistance.
【０００３】通常のステンレス鋼量産工程では、熱間に
おける鋼帯の靭性の低下の問題などから、５％以上のＡ
ｌを含有するフェライトステンレス鋼を製造することは
極めて困難である。これを解決する手段として、製造性
に優れる低Ａｌ含有ステンレス鋼にＡｌをクラッドし、
所定の厚さまで冷間圧延した後に拡散熱処理を行って、
製造性を損なうことなく高Ａｌ含有ステンレス鋼を得る
製造方法が、特開平２−１３３５６２及び特開平２−１
３３５６３に開示されている。In a normal mass production process of stainless steel, A of 5% or more is caused due to the problem of deterioration of toughness of the steel strip during hot working.
It is extremely difficult to produce ferritic stainless steel containing l. As a means for solving this, stainless steel with low Al content, which is excellent in manufacturability, is clad with Al,
After cold rolling to a predetermined thickness, perform diffusion heat treatment,
A method for producing a high Al content stainless steel without impairing manufacturability is disclosed in JP-A-2-133562 and JP-A2-1.
No. 33563.
【０００４】特開平２−１３３５６２および特開平２−
１３３５６３の製造方法は、ステンレス鋼の両面もしく
は片面に、含有させるＡｌ量に相当する割合となるよう
にＡｌもしくはＡｌ合金板を重ね合わせ、これをロール
間に通板して積層圧接板とし、得られた積層圧接板（ク
ラッド材）もしくはこれを圧延した板を、６００〜１３
００℃の温度の範囲において、Ａｌ層が溶融せずに合金
化する条件下で、拡散熱処理を施すことからなる高Ａｌ
含有ステンレス鋼の製造方法である。この発明では、母
材となるステンレス鋼として、Ａｌを含有しないフェラ
イトステンレス鋼を使用することも、クラッド材の圧延
・成形上有利とされている。また、同公報中の実施例で
は、１mm厚のＳＵＳ４３０鋼板を素材として、０．０５
〜０．２０mm厚のＡｌ板をクラッドし、０．３mmまで圧
延した後に拡散熱処理して得た高Ａｌ含有フェライトス
テンレスの耐高温酸化性が、ＳＵＳ４３０に比べて優れ
ているとしている。JP-A-2-133562 and JP-A-2-13362
The manufacturing method of 133563 is obtained by stacking Al or Al alloy plates on both sides or one side of stainless steel in a ratio corresponding to the amount of Al to be contained, and passing this between rolls to form a laminated pressure welding plate. The laminated pressure welding plate (clad material) or the rolled plate is
In the temperature range of 00 ° C., a high Al content obtained by performing a diffusion heat treatment under the condition that the Al layer is alloyed without melting.
It is a method for producing contained stainless steel. In the present invention, the use of ferritic stainless steel that does not contain Al as the stainless steel that is the base material is also advantageous in rolling and forming the clad material. In the example of the publication, a 1 mm-thick SUS430 steel plate is used as a material, and
It is said that the high Al content ferritic stainless steel obtained by clad an Al plate having a thickness of up to 0.20 mm, rolling it to 0.3 mm, and then subjecting it to diffusion heat treatment has superior high-temperature oxidation resistance to SUS430.
【０００５】[0005]
【発明が解決しようとする課題】しかし、Ａｌもしくは
Ａｌ合金（両者を合わせてＡｌと総称する）とステンレ
スからなる積層圧接板（クラッド材）に占めるＡｌ厚さ
が厚かったり、クラッド圧延時から拡散熱処理時までの
全圧延率が高すぎる場合には、クラッド材におけるステ
ンレス相の形状が不均一になる（ステンレス層がくびれ
て厚さが不均一になる）という問題が生じる。この圧延
クラッド材の形状不均一は、日本金属学会会報第２６巻
第１１号、塑性と加工第２９巻第３３２号などで報告さ
れている。この問題は、クラッド材構成相の塑性変形抵
抗の違いにより生ずるものである。ステンレス相がくび
れると、クラッド材中において、ステンレス相の板厚お
よびＡｌ被覆量の変動を生じ、その結果、拡散熱処理後
の高Ａｌ含有ステンレス綱中のＡｌ量が不均一になる。
また，得られた製品の板厚変動が大きくなるため、箔の
耐高温酸化性や電熱性、成形加工性が劣化する問題があ
る。However, the Al thickness occupying the laminated pressure-bonded plate (clad material) made of Al or Al alloy (both are collectively referred to as Al) and stainless steel is large, or diffusion occurs during clad rolling. If the total rolling ratio up to the heat treatment is too high, there arises a problem that the shape of the stainless phase in the clad material becomes nonuniform (the stainless steel layer becomes constricted and the thickness becomes nonuniform). This non-uniform shape of the rolled clad material has been reported in the Japan Institute of Metals, Vol. 26, No. 11, plasticity and working vol. 29, No. 332. This problem is caused by the difference in plastic deformation resistance of the clad material constituent phases. When the stainless phase is constricted, the plate thickness of the stainless phase and the Al coating amount change in the clad material, and as a result, the Al amount in the high Al content stainless steel after diffusion heat treatment becomes non-uniform.
Further, since the thickness variation of the obtained product becomes large, there is a problem that the high temperature oxidation resistance, electric heat resistance, and moldability of the foil deteriorate.
【０００６】一般に、Ａｌ拡散熱処理は真空中もしくは
還元性雰囲気中で行うことが常識的であるが、拡散熱処
理には時間を要するため、長時間このような特殊雰囲下
で熱処理することは生産性を悪化させる要因となる。生
産性を上げようとして、処理温度の上昇により拡散熱処
理に要する時間を短縮しようとすると、箔の変形や箔同
士の固相接合が起こりやすくなるため、鋼板をまいたま
まのコイル状態での処理が困難となる。また昇温速度の
上昇により熱処理時間短縮を図ろうとすると、Ａｌの融
点以上の温度域でＡｌ溶融を生じやすく、溶融したＡｌ
が流れることにより製品中におけるＡｌ含有量の不均一
を生ずる問題もあった。Generally, it is common sense that the Al diffusion heat treatment is performed in a vacuum or in a reducing atmosphere, but since the diffusion heat treatment requires time, it is not possible to perform heat treatment in such a special atmosphere for a long time. It becomes a factor that deteriorates sex. If you try to shorten the time required for diffusion heat treatment by increasing the processing temperature in order to increase productivity, deformation of the foil and solid-phase joining of the foils easily occur, so processing in the coil state with the steel sheet sprinkled Will be difficult. Also, if an attempt is made to shorten the heat treatment time by increasing the temperature rising rate, Al melting tends to occur in the temperature range above the melting point of Al, and the molten Al
There is also a problem in that the Al content in the product is non-uniform due to the flowing of.
【０００７】本発明は、Ａ１含有量分布の均一性に優
れ、かつ板厚変動が小さく、優れた耐高温酸化性と電熱
性を有するフェライトステンレス鋼箔の製造方法を、提
供することを目的とする。An object of the present invention is to provide a method for producing a ferritic stainless steel foil having excellent uniformity of A1 content distribution, small variation in plate thickness, and excellent high temperature oxidation resistance and electric heat resistance. To do.
【０００８】[0008]
【課題を解決するための手段及び作用】上記課題を解決
するため、本発明のフェライトステンレス鋼箔の製造方
法は、フェライトステンレス鋼薄板（原板）の表面にＡ
１泊を圧接してクラッド材を得るクラッド工程と、得ら
れたクラッド材を加熱してＡ１をフェライトステンレス
鋼中に拡散浸透させる拡散熱処理工程とを含む、厚さ３
０〜２００μｍの高Ａ１含有（５％越え）フェライトス
テンレス鋼箔の製造方法であって；Ａ１箔の厚さを１０
〜５０μｍとし、Ａ１箔の硬さをＨｖ４０以下とし、ク
ラッド素材（原板とＡ１箔）から拡散熱処理工程時まで
の全圧延率を１５〜８７％とし、クラッド材のＡ１／ク
ラッド材板厚比を０．１２以下とする、ことを特徴とす
る。In order to solve the above problems, in the method for producing a ferritic stainless steel foil of the present invention, A is formed on the surface of a ferritic stainless steel thin plate (original plate).
Thickness 3 including a clad step of pressing overnight to obtain a clad material and a diffusion heat treatment step of heating the obtained clad material to diffuse and infiltrate A1 into ferritic stainless steel
A method for producing a ferritic stainless steel foil having a high A1 content (more than 5%) of 0 to 200 μm; the thickness of the A1 foil is 10
To 50 μm, the hardness of the A1 foil is Hv40 or less, the total rolling rate from the clad material (original plate and A1 foil) to the diffusion heat treatment step is 15 to 87%, and the A1 / clad material plate thickness ratio of the clad material is It is characterized in that it is 0.12 or less.
【０００９】本発明の主旨は、クラッド素材にＡｌを含
有するフェライトステンレス鋼帯を使用して、含有させ
るＡｌ量を得るのに必要なＡｌもしくはＡｌ合金帯の板
厚を小さくし、なおかつ素材厚を小さくすることにより
クラッド圧延時から拡散熱処理時の箔までの累積圧延率
を低くして、クラッド材におきるステンレス相の形状不
均一（くびれ）発生を抑え、拡散熱処理後のＡｌ量不均
一および板厚変動を抑えるものである。The gist of the present invention is to use a ferritic stainless steel strip containing Al as a clad material to reduce the plate thickness of the Al or Al alloy strip necessary to obtain the amount of Al to be contained, and to reduce the material thickness. By decreasing the value, the cumulative rolling ratio from the clad rolling to the foil during the diffusion heat treatment is reduced, the occurrence of non-uniform shape (constriction) of the stainless phase in the clad material is suppressed, and the Al amount after the diffusion heat treatment is non-uniform. It suppresses plate thickness variation.
【００１０】本発明においては上記拡散熱処理工程にお
いては、処理雰囲気を大気とし、昇温速度を１０℃／mi
n 以下とし、保持温度を８５０〜１０００℃とすること
が好ましい。In the present invention, in the diffusion heat treatment step, the treatment atmosphere is atmospheric air and the temperature rising rate is 10 ° C./mi.
It is preferable that the temperature is not more than n and the holding temperature is 850 to 1000 ° C.
【００１１】本発明者等は、Ａｌ／ＳＵＳクラッド帯の
拡散熱処理方法を詳細に検討した結果、拡散熱処理時の
雰囲気を大気雰囲気とすることによりＡｌクラッド材の
Ａｌ層表層部にＡｌ酸化物の層を形成させ、これをＡｌ
溶融層流出を防止しうるの物理的被覆にすることができ
ることを知見した。この酸化物の皮覆によりＡｌ溶融を
生じる昇温速度で加熱しても、溶融したＡｌがある程度
保持され、高い昇温速度で熱処理する際のＡｌ溶融によ
るＡｌ含有量不均一を抑えうる。これにより拡散熱処理
時間が短縮されて生産性が上り、なおかつ雰囲気を大気
中とするため製造コストが下がる。As a result of a detailed study of the diffusion heat treatment method for the Al / SUS clad zone, the present inventors have found that the atmosphere during the diffusion heat treatment is an air atmosphere, so that an Al oxide layer is formed on the surface of the Al layer of the Al clad material. Form a layer and
It has been found that a physical coating can be provided which can prevent the outflow of the molten layer. Even when heated at a temperature rising rate that causes Al melting due to the covering of the oxide, the molten Al is retained to some extent, and uneven Al content due to Al melting during heat treatment at a high temperature rising rate can be suppressed. As a result, the diffusion heat treatment time is shortened and the productivity is increased, and since the atmosphere is the atmosphere, the manufacturing cost is reduced.
【００１２】本発明の対象とする高Ａｌ含有フェライト
ステンレス鋼箔（帯）は、Ａｌ含有量が５％を越え、か
つ板厚が３０〜２００μｍである。５％程度以下のＡｌ
含有量であれば通常のステンレス量産工程で工業的に製
造可能であり、かつそのほうが生産性に優れかつ安価だ
からである。板厚の範囲については、板厚が２００μｍ
を越えると，板厚方向にＡｌが均一に拡散しにくく、表
層部に硬く脆い高Ａｌ部が残留するため、著しく延性を
劣化させる。３０μｍ以下では拡散熱処理時に箔変形を
生じやすく、良好な製品を得にくくなる。The high Al content ferritic stainless steel foil (band) to which the present invention is applied has an Al content of more than 5% and a plate thickness of 30 to 200 μm. Al less than about 5%
This is because if it is contained, it can be industrially produced by a normal stainless steel mass production process, and that is more excellent in productivity and cheaper. Regarding the thickness range, the thickness is 200 μm
When it exceeds, the Al hardly diffuses uniformly in the plate thickness direction, and a hard and brittle high Al portion remains on the surface layer portion, so that ductility is significantly deteriorated. If it is 30 μm or less, foil deformation is likely to occur during diffusion heat treatment, and it becomes difficult to obtain a good product.
【００１３】本発明では、ステンレス量産工程で生産が
容易な範囲のＡｌを含有するフェライトステンレス鋼帯
をクラッド素材とすることが好ましい。フェライトステ
ンレス鋼はオーステナイト鋼に比べＡｌ拡散が容易であ
るので、拡散熱処理が低温短時間で行える。そのため本
発明の対象素材として有利である。素材のフェライトス
テンレス鋼に含有させるＡｌ量は特に限定されないが、
５％程度を越えるＡｌを含有するステンレス鋼の製造は
一般のステンレス量産工程では困難であるので、クラッ
ド素材フェライトステンレス鋼のＡｌ含有量は５％程度
以下がのぞましい。また、耐高温酸化性を向上するた
め、鋼中にＲＥＭを添加してもよい。In the present invention, it is preferable to use, as a clad material, a ferritic stainless steel strip containing Al in a range that is easily produced in a mass production process of stainless steel. Since ferritic stainless steel diffuses Al more easily than austenitic steel, diffusion heat treatment can be performed at low temperature in a short time. Therefore, it is advantageous as a target material of the present invention. Although the amount of Al contained in the material ferritic stainless steel is not particularly limited,
Since the production of stainless steel containing Al in excess of about 5% is difficult in a general mass production process of stainless steel, the Al content of the clad material ferritic stainless steel is preferably about 5% or less. Further, in order to improve the high temperature oxidation resistance, REM may be added to the steel.
【００１４】本発明では、Ａｌ（Ａ１合金含む）箔の成
分は特に制限されない。耐高温酸化性改良の観点から
は、Ｚｒ、Ｓｉなどを微量添加したＡｌ合金箔を用いて
もよい。In the present invention, the components of the Al (including A1 alloy) foil are not particularly limited. From the viewpoint of improving the high temperature oxidation resistance, an Al alloy foil to which a trace amount of Zr, Si or the like is added may be used.
【００１５】本発明では、Ａｌ箔の厚さを１０〜５０μ
ｍとする。１０μｍ未満ではクラッド圧延時にしわが発
生しやすい。５０μｍを越える場合、クラッド圧延後の
冷間圧延時にＡｌが剥離しない程度のＡｌ／ＳＵＳ間の
接合力を得ために必要なクラッド圧延率が上昇するた
め、クラッド圧延時に圧延材が蛇行し形状制御しにくく
なる。In the present invention, the thickness of the Al foil is 10 to 50 μm.
m. If it is less than 10 μm, wrinkles are likely to occur during clad rolling. If it exceeds 50 μm, the clad rolling rate necessary to obtain the joining force between Al and SUS at which Al does not separate during cold rolling after clad rolling increases, so the rolled material meanders during clad rolling and shape control is performed. Hard to do.
【００１６】本発明ではＡｌもしくはＡｌ合金箔の硬さ
をＨｖ４０以下とし、例えば焼なまし材を箔素材とす
る。ビッカース硬さＨｖ４０を越える硬質材を用いると
クラッド圧延後にさらに圧延して箔とする場合に、箔圧
延時にＡｌ剥離が生じ易く、製造性が著しく低くなる。
また、クラッド材の接合力を強化するために熱処理を施
す場合でも、硬質材ではフクレが発生しやすく、箔圧延
時に剥離を生じる。クラッド圧延後に圧延を行わない場
合でも、Ａｌ拡散熱処理時の昇温過程においてフクレを
生じ、このフクレ部分のＡｌが溶融してＡｌ量不均一の
原因となる。一般には、強固な接合力を得るのに必要な
圧延率は室温下で３０〜４０％以上とされているが、本
発明の製造条件では、１５％〜２０％のクラッド圧延率
で同等のＡｌ／ＳＵＳ間接合力が得られ、冷間圧延時に
Ａｌが剥離しない。そのため、蛇行制御および形状制御
が容易となりＡｌのしわ発生を防止できる。これは、圧
延材表層部の加工度が、圧延材内部の加工度に比べて高
いため、クラッド圧延時に、接合に必要な新生面がより
生じやすいことによると考えられる。また、Ａｌ帯が薄
いため、ロールの圧延時の発熱が、Ａｌ／ＳＵＳ界面に
伝達しやすく、接合に対して有利に作用しているためと
考えられる。クラッド素材の加熱もしくはクラッド圧延
後の熱処理により、低い圧延率でも強固な接合力を得る
方法は公知であるが、本発明によればこれらの熱処理は
省略できる。In the present invention, the hardness of the Al or Al alloy foil is set to Hv 40 or less and, for example, the annealed material is used as the foil material. When a hard material having a Vickers hardness of more than Hv40 is used, when the foil is further rolled after clad rolling to form a foil, Al peeling is likely to occur during foil rolling, resulting in significantly low productivity.
Further, even when heat treatment is performed to enhance the bonding strength of the clad material, blistering is likely to occur in the hard material and peeling occurs during foil rolling. Even if the rolling is not performed after the clad rolling, blisters are generated in the temperature rising process during the Al diffusion heat treatment, and the Al in the blisters is melted, which causes a nonuniform Al amount. Generally, the rolling rate required to obtain a strong joining force is set to 30 to 40% or more at room temperature, but under the manufacturing conditions of the present invention, an equivalent Al with a clad rolling rate of 15% to 20% is used. / SUS bonding strength is obtained, and Al does not peel off during cold rolling. Therefore, the meandering control and the shape control are facilitated, and the generation of Al wrinkles can be prevented. It is considered that this is because the workability of the surface portion of the rolled material is higher than the workability of the inside of the rolled material, so that a new surface required for joining is more likely to be formed during clad rolling. Further, it is considered that since the Al band is thin, the heat generated during rolling of the roll is easily transmitted to the Al / SUS interface, which has an advantageous effect on the joining. Although a method of obtaining a strong joining force even at a low rolling rate by heating the clad material or heat treatment after clad rolling is known, these heat treatments can be omitted according to the present invention.
【００１７】本発明では、クラッド材のＡｌ／クラッド
板厚比率を〜０．１２以下とし、なおかつ、クラッド素
材から高Ａｌ含有鋼フェライトステンレス鋼箔（クラッ
ド箔）までの総合圧延率を１５〜８７％とする。In the present invention, the Al / clad plate thickness ratio of the clad material is set to 0.12 or less, and the total rolling ratio from the clad material to the high Al content steel ferrite stainless steel foil (clad foil) is 15 to 87. %.
【００１８】本発明の素材厚および製品厚の範囲内で
は、圧延率８７％越え、もしくは、Ａｌ／クラッド板厚
比率０．１２越えの場合、クラッド材におけるステンレ
ス相のくびれが生じ、Ａｌ／ＳＵＳ板厚比がクラッド帯
長手方向で変動する。累計圧延率が１５％未満では、ク
ラッド圧延後に圧延を行う場合、Ａｌ剥離防止のために
温間クラッドないしクラッド圧延後の熱処理が必要とな
り、生産性が低下する。また、クラッド圧延後に圧延を
行わない場合は、累計圧延率１５％未満では拡散熱処理
時の昇温の際にふくれを生じ、これがＡｌ溶融をおこし
てＡｌ含有量の不均一を招き易い。Within the range of the material thickness and the product thickness of the present invention, when the rolling ratio exceeds 87% or the Al / clad plate thickness ratio exceeds 0.12, a constriction of the stainless phase in the clad material occurs, resulting in Al / SUS. The plate thickness ratio varies in the longitudinal direction of the clad zone. If the cumulative rolling rate is less than 15%, when performing rolling after clad rolling, warm clad or heat treatment after clad rolling is required to prevent Al delamination, resulting in reduced productivity. Further, when the rolling is not performed after the clad rolling, if the cumulative rolling ratio is less than 15%, swelling occurs at the time of temperature rise during the diffusion heat treatment, and this causes Al melting to easily cause nonuniformity of the Al content.
【００１９】本発明の一態様の拡散熱処理工程において
は、拡散熱処理温度の範囲を８５０〜１０００℃とす
る。８５０℃未満ではＡｌ拡散が遅く、また１０００℃
越えでは、箔変形ないし箔どうしの固相接合が生じる。
最も耐高温酸化性が優れる、８５０〜９５０℃前後が最
適である。In the diffusion heat treatment step of one embodiment of the present invention, the diffusion heat treatment temperature range is 850 to 1000 ° C. Al diffusion is slow below 850 ° C, and 1000 ° C
At the crossing point, foil deformation or solid-phase bonding between foils occurs.
The optimum temperature is around 850 to 950 ° C, which has the highest resistance to high-temperature oxidation.
【００２０】本発明の一態様の拡散熱処理工程において
は、拡散熱処理の雰囲気を大気中とする。真空中もしく
は還元性雰囲気中ではＡｌ表面に生成させる酸化物層の
厚さが十分でなく、溶融Ａｌを保持できない。ただし、
シート材の回りに大気が流動しやすい状態で熱処理した
のでは、過度に表面が酸化されＡｌ消費量が大きくなる
ので、タイトに巻いたコイルの状態で拡散熱処理するこ
とが望ましい。さらに、その際の巻取張力は５（３〜
７）ｋｇ／ｍｍ2 前後が望ましい。張力が過度に高い場
合、拡散熱処理材の変形、固相接合などの問題を生ずる
からある。In the diffusion heat treatment step of one embodiment of the present invention, the atmosphere of the diffusion heat treatment is atmospheric air. In vacuum or in a reducing atmosphere, the thickness of the oxide layer formed on the Al surface is not sufficient and molten Al cannot be retained. However,
If the heat treatment is performed in a state where the air flows around the sheet material easily, the surface is excessively oxidized and the amount of Al consumed becomes large. Therefore, it is desirable to perform the diffusion heat treatment in the state of a tightly wound coil. Furthermore, the winding tension at that time is 5 (3 ~
7) About kg / mm 2 is desirable. This is because if the tension is excessively high, problems such as deformation of the diffusion heat treatment material and solid-phase bonding may occur.
【００２１】本発明の一態様の拡散熱処理工程において
は、拡散熱処理時の昇温速度を〜１０℃／ｍｉｎとす
る。１０℃／ｍｉｎを越えると、Ａｌ表面に生成させた
酸化物層で溶融Ａｌを保持できなくなる。。相互拡散に
よるＡｌ層のＦｅ−Ａｌ合金化の速度が溶融Ａｌの生成
速度に比べて遅いためと考えられる。昇温速度の下限値
は、５℃／ｍｉｎが好ましい。それ未満では、拡散熱処
理の昇温に要する時間が長くなり生産性が低下する。In the diffusion heat treatment step of one embodiment of the present invention, the rate of temperature rise during the diffusion heat treatment is set to -10 ° C / min. If it exceeds 10 ° C / min, the molten Al cannot be retained by the oxide layer formed on the Al surface. . It is considered that the rate of Fe—Al alloying of the Al layer by mutual diffusion is slower than the rate of formation of molten Al. The lower limit of the heating rate is preferably 5 ° C / min. If it is less than that, the time required for raising the temperature of the diffusion heat treatment becomes long and the productivity is lowered.
【００２２】[0022]
実施例１ 表１に示す組成のフェライトステンレス鋼帯の両表面を
ロールブラシにて研磨し、この両面に表２に示す組成の
Ａｌ箔帯を、表３に示す板厚構成および圧延率で冷間ク
ラッド圧延した。Example 1 Both surfaces of a ferritic stainless steel strip having the composition shown in Table 1 were polished with a roll brush, and Al foil strips having the composition shown in Table 2 were cooled on both sides with the plate thickness configuration and rolling rate shown in Table 3. Clad rolled.
【００２３】[0023]
【表１】 [Table 1]
【００２４】[0024]
【表２】 [Table 2]
【００２５】[0025]
【表３】 [Table 3]
【００２６】次に得られたクラッドコイルを、常法に従
い、表３に示す板厚まで冷間圧延した。その後、拡散熱
処理として、大気中にて昇温速度１０℃／ｍｉｎにて９
００℃まで加熱、これを６時間保持した後に冷却した。
Ａｌ量、その均一性の結果を第３表に示した。発明材は
クラッド箔のステンレス相にくびれを生じなかった。El
ectron Prove Micro AnalyzerノLine ProfileにてＡｌ濃
度の勾配の有無を調査した結果、拡散熱処理後のＡｌ含
有量が板厚方向、面方向ともに均一であることを確認を
した。Next, the obtained clad coil was cold-rolled to a plate thickness shown in Table 3 by a conventional method. Then, as a diffusion heat treatment, the temperature was raised in the atmosphere at a temperature rising rate of 10 ° C./min for 9
It was heated to 00 ° C., kept for 6 hours and then cooled.
Table 3 shows the results of the amount of Al and its uniformity. The invention material did not cause a necking in the stainless phase of the clad foil. El
As a result of investigating the presence or absence of a gradient of Al concentration by ectron Prove Micro Analyzer No Line Profile, it was confirmed that the Al content after the diffusion heat treatment was uniform in both the plate thickness direction and the surface direction.
【００２７】本発明の製造条件の範囲では、冷間クラッ
ド圧延の圧延率が２０％以下でも、その後の冷間圧延に
てＡｌ剥離しない程度の十分なＡｌ／ＳＵＳ間接合力が
得られることを確認した。It was confirmed that within the range of the manufacturing conditions of the present invention, even if the rolling ratio of cold clad rolling is 20% or less, a sufficient Al / SUS joining force that does not cause Al peeling in the subsequent cold rolling can be obtained. did.
【００２８】比較材である試料３では、累計圧延率が８
７．２％と高かったため、箔クラッド状態でステンレス
鋼がくびれ、板厚で１０％前後のうねりを生じた。ま
た、９．５〜１２％の範囲でＡｌ濃度がバラツキを生じ
ていた。試料４では、累計圧延率が８７．４％と高く、
またＡｌ層／クラッド板厚比が０．１２３％と高かった
ため、板厚比で１３％のうねりを生じ、また試料３と同
様にＡｌ濃度が不均一であった。素材厚が大きい試料７
および８の製造では、クラッド圧下率が２０％以下では
曲げ試験にてＡｌ剥離してしまう程度の接合力しか得ら
れず、これを冷間圧延したところＡｌが剥離し圧延でき
なかった。試料９では、Ａｌ／クラッド板厚比が１４．
２％と高かったため、クラッド時点でのＡｌとステンレ
スの接合力が十分でなく、また、接合面のくびれも認め
られた。Ｈｖ４２の硬質Ａｌ箔を用いた試料１０では、
クラッド圧延後の圧延にてＡｌ剥離を生じ、これを拡散
熱処理したところ著しい面方向のＡｌ量不均一を生じ
た。試料１１では昇温過程で生じたフクレによる面方向
でのＡｌ量不均一を生じた。Sample 3, which is a comparative material, has a cumulative rolling ratio of 8
Since it was as high as 7.2%, the stainless steel was constricted in the foil clad state, and waviness of about 10% in plate thickness occurred. In addition, the Al concentration varied in the range of 9.5 to 12%. In sample 4, the cumulative rolling rate was as high as 87.4%,
Further, since the Al layer / clad plate thickness ratio was as high as 0.123%, undulation of 13% was generated in the plate thickness ratio, and the Al concentration was non-uniform as in Sample 3. Sample 7 with thick material
In the production of No. 8 and No. 8, when the clad rolling reduction was 20% or less, only a joining force enough to cause Al delamination in the bending test was obtained, and when this was cold-rolled, Al was delaminated and could not be rolled. In Sample 9, the Al / clad plate thickness ratio was 14.
Since it was as high as 2%, the joining force between Al and stainless steel at the time of clad was not sufficient, and constriction of the joining surface was also recognized. In the sample 10 using the hard Al foil of Hv42,
Al peeling occurred in the rolling after the clad rolling, and when this was subjected to diffusion heat treatment, a remarkable unevenness of the Al amount in the surface direction occurred. In Sample 11, unevenness in the amount of Al in the surface direction was generated due to blisters generated during the temperature rising process.
【００２９】実施例２ 実施例１における試料１の素材条件および圧延条件にて
製造した０．０５０ｍｍ厚クラッド箔コイルを、大気中
にて表４に示す熱処理条件にて拡散熱処理を施した。Ａ
ｌ量の均一性等の結果を第４表に示す。Example 2 A 0.050 mm thick clad foil coil manufactured under the material conditions and rolling conditions of Sample 1 in Example 1 was subjected to diffusion heat treatment in the atmosphere under the heat treatment conditions shown in Table 4. A
Table 4 shows the results such as the uniformity of 1 amount.
【００３０】[0030]
【表４】 [Table 4]
【００３１】Ａｌ量均一性については、Electron Prove
Micro Analyzer の Line Profileにて板厚方向および
面方向でＡｌ濃度匂配が認められなかったものを〇とし
た。１０５０℃ならびに１１００℃では箔の変形および
融着接合（試料７、８、９）が生じた。接合した試料は
拡散熱処理後にコイルを巻き戻すことができなかった。
箔変形および融着接合を生じない８５０〜１０００℃の
温度範囲では、６時間程度の保持を行えば板厚方向での
Ａｌ量は均一であるが、１５℃／ｍｉｎを越える昇温速
度で加熱すると、面方向でのＡｌ量が不均一となった
（試料３）。また、８００℃で処理した試料４もＡｌ量
が不均一となった。発明材（試料１、２、５、６）で
は、板厚方向および面方向でのＡｌ量不均一、箔変形、
融着接合は生じないことを確認した。For the uniformity of the Al amount, see Electron Prove
The line profile of the Micro Analyzer showed that no Al concentration odor was observed in the plate thickness direction and the surface direction, and was designated as ◯. At 1050 ° C and 1100 ° C, foil deformation and fusion bonding (Samples 7, 8, 9) occurred. The bonded sample was unable to unwind the coil after diffusion heat treatment.
In the temperature range of 850 to 1000 ° C. where foil deformation and fusion bonding do not occur, the amount of Al in the plate thickness direction is uniform if held for about 6 hours, but heating is performed at a heating rate exceeding 15 ° C./min. Then, the amount of Al in the plane direction became nonuniform (Sample 3). Further, the sample 4 processed at 800 ° C. also had an uneven Al amount. In the invention materials (Samples 1, 2, 5, and 6), uneven Al amount in the plate thickness direction and the surface direction, foil deformation,
It was confirmed that fusion bonding did not occur.
【００３２】[0032]
【発明の効果】以上の説明から明らかなように、本発明
は、クラッド材におきるステンレス相の形状不均一（く
びれ）発生を抑えることができるので、Ａ１含有量分布
の均一性に優れ、かつ板厚変動が小さく、優れた耐高温
酸化性と電熱性を有するフェライトステンレス鋼箔を提
供することができる。As is apparent from the above description, the present invention can suppress the occurrence of non-uniform shape (constriction) of the stainless phase in the clad material, so that the A1 content distribution is excellent in uniformity and It is possible to provide a ferritic stainless steel foil having a small thickness variation and excellent high-temperature oxidation resistance and electric heat resistance.
Claims (2)
表面にＡｌ箔を圧接してクラッド材を得るクラッド工程
と、 得られたクラッド材を加熱してＡｌをフェライトステン
レス鋼中に拡散浸透させる拡散熱処理工程とを含む、 厚さ３０〜２００μm の高Ａｌ含有（５％越え）フェラ
イトステンレス鋼箔の製造方法であって；Ａｌ箔の厚さ
を１０〜５０μm とし、 Ａｌ箔の硬さをＨｖ４０以下とし、 クラッド素材（原板とＡｌ箔）から拡散熱処理工程時ま
での全圧延率を１５〜８７％とし、 クラッド材のＡｌ／クラッド材板厚比を０．１２以下と
する、ことを特徴とする高Ａｌ含有フェライトステンレ
ス鋼箔の製造方法。1. A clad step of pressing an Al foil onto the surface of a ferritic stainless steel thin plate (original plate) to obtain a clad material, and a diffusion heat treatment for heating the obtained clad material to diffuse and permeate Al into the ferritic stainless steel. A method for producing a high Al content (more than 5%) ferritic stainless steel foil having a thickness of 30 to 200 μm, including the steps; the thickness of the Al foil is 10 to 50 μm, and the hardness of the Al foil is Hv40 or less. The total rolling ratio from the clad material (original plate and Al foil) to the diffusion heat treatment step is 15 to 87%, and the Al / clad material plate thickness ratio of the clad material is 0.12 or less. Method for producing Al-containing ferritic stainless steel foil.
高Ａｌ含有フェライトステンレス鋼箔の製造方法。2. The high Al-containing ferritic stainless steel foil according to claim 1, wherein in the diffusion heat treatment step, a treatment atmosphere is atmospheric air, a temperature rising rate is 10 ° C./min or less, and a holding temperature is 850 to 1000 ° C. Manufacturing method.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP5349243A JP2822141B2 (en) | 1993-12-28 | 1993-12-28 | Method for producing high Al-containing ferritic stainless steel foil |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP5349243A JP2822141B2 (en) | 1993-12-28 | 1993-12-28 | Method for producing high Al-containing ferritic stainless steel foil |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH07185839A true JPH07185839A (en) | 1995-07-25 |
| JP2822141B2 JP2822141B2 (en) | 1998-11-11 |
Family
ID=18402451
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP5349243A Expired - Fee Related JP2822141B2 (en) | 1993-12-28 | 1993-12-28 | Method for producing high Al-containing ferritic stainless steel foil |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP2822141B2 (en) |
Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP0837151A1 (en) * | 1996-10-15 | 1998-04-22 | Krupp VDM GmbH | Process for the manufacture of a iron-chrome-aluminium foil and its use |
| EP0861916A1 (en) * | 1997-02-28 | 1998-09-02 | Usinor | Process for making a stainless steel strip rich in aluminium especially suitable for a catalytic converter support for a motor vehicle |
| FR2806940A1 (en) * | 2000-03-29 | 2001-10-05 | Usinor | Ferritic stainless steel sheet containing aluminium and rare earth metals suitable for use in the catalyst support elements of motor vehicle exhaust systems |
| US7353981B2 (en) * | 2004-01-15 | 2008-04-08 | All-Clad Metalcrafters Llc | Method of making a composite metal sheet |
| JP2008537977A (en) * | 2005-03-11 | 2008-10-02 | アルセロールミタル・フランス | Method for producing coated steel member with extremely high resistance after heat treatment |
| JP2014216354A (en) * | 2013-04-22 | 2014-11-17 | オムロン株式会社 | Magnetic component, electronic component using the magnetic component, and method for producing the magnetic component |
Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH0313559A (en) * | 1989-06-13 | 1991-01-22 | Nisshin Steel Co Ltd | Production of ferritic stainless steel sheet with high al content or formed part of the same |
-
1993
- 1993-12-28 JP JP5349243A patent/JP2822141B2/en not_active Expired - Fee Related
Patent Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH0313559A (en) * | 1989-06-13 | 1991-01-22 | Nisshin Steel Co Ltd | Production of ferritic stainless steel sheet with high al content or formed part of the same |
Cited By (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP0837151A1 (en) * | 1996-10-15 | 1998-04-22 | Krupp VDM GmbH | Process for the manufacture of a iron-chrome-aluminium foil and its use |
| EP0861916A1 (en) * | 1997-02-28 | 1998-09-02 | Usinor | Process for making a stainless steel strip rich in aluminium especially suitable for a catalytic converter support for a motor vehicle |
| FR2760244A1 (en) * | 1997-02-28 | 1998-09-04 | Usinor | METHOD FOR MANUFACTURING A FERRITIC STAINLESS STEEL SHEET WITH A HIGH ALUMINUM CONTENT FOR USE IN PARTICULAR FOR A MOTOR VEHICLE EXHAUST CATALYST SUPPORT |
| FR2806940A1 (en) * | 2000-03-29 | 2001-10-05 | Usinor | Ferritic stainless steel sheet containing aluminium and rare earth metals suitable for use in the catalyst support elements of motor vehicle exhaust systems |
| US7353981B2 (en) * | 2004-01-15 | 2008-04-08 | All-Clad Metalcrafters Llc | Method of making a composite metal sheet |
| JP2008537977A (en) * | 2005-03-11 | 2008-10-02 | アルセロールミタル・フランス | Method for producing coated steel member with extremely high resistance after heat treatment |
| JP2014216354A (en) * | 2013-04-22 | 2014-11-17 | オムロン株式会社 | Magnetic component, electronic component using the magnetic component, and method for producing the magnetic component |
Also Published As
| Publication number | Publication date |
|---|---|
| JP2822141B2 (en) | 1998-11-11 |
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