JPH06330246A - Fe-cr-al alloy excellent in high temperature strength after brazing and oxidation resistance - Google Patents
Fe-cr-al alloy excellent in high temperature strength after brazing and oxidation resistanceInfo
- Publication number
- JPH06330246A JPH06330246A JP11809993A JP11809993A JPH06330246A JP H06330246 A JPH06330246 A JP H06330246A JP 11809993 A JP11809993 A JP 11809993A JP 11809993 A JP11809993 A JP 11809993A JP H06330246 A JPH06330246 A JP H06330246A
- Authority
- JP
- Japan
- Prior art keywords
- less
- oxidation resistance
- alloy
- brazing
- high temperature
- 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.)
- Withdrawn
Links
Landscapes
- Heat Treatment Of Sheet Steel (AREA)
Abstract
Description
【０００１】[0001]
【産業上の利用分野】本発明は、ろう付け後の高温強度
および耐酸化性に優れたＦｅ−Ｃｒ−Ａｌ系合金板およ
びその箔に関する。本合金はろう付けによって組み立て
られる部品の材料であり、高温酸化性雰囲気下で激しい
振動、熱刺激を受ける自動車排ガス浄化用触媒担体およ
び触媒コンバータに好適である。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a Fe-Cr-Al alloy plate excellent in high temperature strength and oxidation resistance after brazing and a foil thereof. The present alloy is a material for components assembled by brazing, and is suitable for a catalyst carrier and a catalytic converter for purifying automobile exhaust gas that are subjected to severe vibration and thermal stimulation in a high temperature oxidizing atmosphere.
【０００２】[0002]
【従来の技術】近年、自動車排ガス浄化触媒装置の担体
としてＦｅ−Ｃｒ−Ａｌ系合金箔をろう付けによってハ
ニカム状に組み立てた担体が採用されつつある。しか
し、自動車排ガス規制の強化により、特にコールドスタ
ート時の排ガス浄化効率を向上させることが必要とされ
ている。そのため、自動車排ガス浄化触媒装置はコンバ
ータを燃焼環境に近い位置に設置し、高温の排ガスによ
りエンジン始動初期より早い時期に触媒活性化温度に到
達させ、触媒反応を起こさせるものが開発されつつあ
る。また、エンジンの高出力化および小型化によるエン
ジン振動および排ガス衝撃の増大していることから、従
来のＦｅ−Ａｌ−Ｃｒ合金ではその高温強度が不足し、
ハニカム破損が生じて実用化できない。2. Description of the Related Art In recent years, a carrier in which a Fe--Cr--Al alloy foil is assembled in a honeycomb shape by brazing is being used as a carrier for an automobile exhaust gas purification catalyst device. However, it is necessary to improve the exhaust gas purification efficiency especially at the cold start by strengthening the automobile exhaust gas regulations. Therefore, an automobile exhaust gas purification catalyst device is being developed in which a converter is installed in a position close to the combustion environment, and the exhaust gas of high temperature reaches the catalyst activation temperature earlier than the initial stage of engine startup to cause a catalytic reaction. Moreover, since the engine vibration and exhaust gas impact are increasing due to the high output and downsizing of the engine, the conventional Fe-Al-Cr alloy lacks high temperature strength,
The honeycomb breaks and cannot be put to practical use.
【０００３】素材自身の強度をＮｂ添加により改善して
いる例が、特開平４−１２０２４７号および特開昭５８
−１７７４３７号に開示されている。しかし、ろう付け
によって組み立てられた箔材は、粒界強度が著しく低下
し、ハニカムが破損してしまう。Examples in which the strength of the material itself is improved by adding Nb are disclosed in JP-A-4-120247 and JP-A-58.
No. 177437. However, the grain boundary strength of the foil material assembled by brazing is significantly reduced, and the honeycomb is damaged.
【０００４】[0004]
【発明が解決しようとする課題】以上のように、従来の
Ｆｅ−Ｃｒ−Ａｌ合金をろう付けによって使用する場
合、強度不足のため実用に耐えない。本発明は上述した
従来技術の欠点を解消した高温での強度および耐酸化性
に優れたＦｅ−Ｃｒ−Ａｌ合金、特に触媒担体用材料と
して好適な、板厚が０．５ｍｍ以下のＦｅ−Ｃｒ−Ａｌ
合金板および０．１ｍｍ以下の箔を提供することを目的
とする。また、本材料はろう付けによって組み立てられ
る燃焼ガス排気系の機器、装置としても好ましい。As described above, when a conventional Fe-Cr-Al alloy is used by brazing, it cannot be put to practical use because of insufficient strength. The present invention solves the above-mentioned drawbacks of the prior art and is excellent in strength and oxidation resistance at high temperatures. Fe—Cr—Al alloys, particularly Fe—Cr having a plate thickness of 0.5 mm or less, which is suitable as a material for catalyst carriers. -Al
The purpose is to provide an alloy plate and a foil of 0.1 mm or less. Further, this material is also preferable as a device or apparatus for a combustion gas exhaust system assembled by brazing.
【０００５】[0005]
【課題を解決するための手段】本発明の第一の態様によ
れば、重量％で、 Ｃ：０．０５％以下、 Ｓｉ：１．５％以下 Ｍｎ：１．０％以下、 Ｃｒ：１１．０〜２６％ Ａｌ：１．０〜８．０％、 Ｎ：０．０３％以下 Ｔｉ：０．０１〜２．０％、Ｚｒ：０．０１〜２．０％ Ｔｉ＋Ｚｒの総量が、１．５％＜Ｔｉ＋Ｚｒ≦３．０％
を満たし、 Ｌａ：０．０５〜０．２％、Ｃｅ：０．０３％以下を含
み、残部Ｆｅおよび不可避的不純物からなることを特徴
とするろう付け後の高温強度および耐酸化性に優れたＦ
ｅ−Ｃｒ−Ａｌ系合金が提供される。According to the first aspect of the present invention, in weight%, C: 0.05% or less, Si: 1.5% or less, Mn: 1.0% or less, Cr: 11 0.0 to 26% Al: 1.0 to 8.0%, N: 0.03% or less Ti: 0.01 to 2.0%, Zr: 0.01 to 2.0% The total amount of Ti + Zr is 1. 0.5% <Ti + Zr ≦ 3.0%
And La: 0.05 to 0.2%, Ce: 0.03% or less, and the balance Fe and unavoidable impurities, and is excellent in high-temperature strength and oxidation resistance after brazing. F
An e-Cr-Al based alloy is provided.
【０００６】本発明の第二の態様によれば、重量％で、 Ｃ：０．０５％以下、 Ｓｉ：１．５％以下 Ｍｎ：１．０％以下、 Ｃｒ：１１．０〜２６％ Ａｌ：１．０〜８．０％、 Ｎ：０．０３％以下 Ｔｉ：０．０１〜２．０％、Ｚｒ：０．０１〜２．０％ Ｔｉ＋Ｚｒの総量が、１．５％＜Ｔｉ＋Ｚｒ≦３．０％ ランタノイド：Ｃｅを０．０３％以下、その他のランタ
ノイド０．００１〜０．０５％の範囲内でかつランタノ
イドの合計が０．０５〜０．２％を含み、残部Ｆｅおよ
び不可避的不純物からなることを特徴とするろう付け後
の高温強度および耐酸化性に優れたＦｅ−Ｃｒ−Ａｌ系
合金が提供される。According to the second aspect of the present invention, in weight%, C: 0.05% or less, Si: 1.5% or less, Mn: 1.0% or less, Cr: 11.0 to 26% Al. : 1.0 to 8.0%, N: 0.03% or less Ti: 0.01 to 2.0%, Zr: 0.01 to 2.0% The total amount of Ti + Zr is 1.5% <Ti + Zr ≦. 3.0% lanthanoid: Ce of 0.03% or less, other lanthanoids within the range of 0.001 to 0.05%, and the total amount of lanthanoids including 0.05 to 0.2%, balance Fe and unavoidable An Fe-Cr-Al based alloy excellent in high temperature strength and oxidation resistance after brazing, which is characterized by comprising impurities, is provided.
【０００７】本発明の第三の態様によれば、重量％で、 Ｃ：０．０５％以下、 Ｓｉ：１．５％以下 Ｍｎ：１．０％以下、 Ｃｒ：１１．０〜２６％ Ａｌ：１．０〜８．０％、 Ｎ：０．０３％以下 Ｔｉ：０．０１〜２．０％、Ｚｒ：０．０１〜２．０％ Ｎｂ：０．０１〜１．５％、 Ｔｉ＋Ｚｒ＋Ｎｂの総量が、１．５％＜Ｔｉ＋Ｚｒ＋Ｎ
ｂ≦３．０％を満たし、 Ｌａ：０．０５〜０．２％、Ｃｅ：０．０３％以下を含
み、残部Ｆｅおよび不可避的不純物からなることを特徴
とするろう付け後の高温強度および耐酸化性に優れたＦ
ｅ−Ｃｒ−Ａｌ系合金が提供される。According to the third aspect of the present invention, in% by weight, C: 0.05% or less, Si: 1.5% or less, Mn: 1.0% or less, Cr: 11.0 to 26% Al. : 1.0 to 8.0%, N: 0.03% or less Ti: 0.01 to 2.0%, Zr: 0.01 to 2.0% Nb: 0.01 to 1.5%, Ti + Zr + Nb Is 1.5% <Ti + Zr + N
b ≦ 3.0%, La: 0.05 to 0.2%, Ce: 0.03% or less, and the balance Fe and inevitable impurities at high temperature strength after brazing and F with excellent oxidation resistance
An e-Cr-Al based alloy is provided.
【０００８】本発明の第四の態様によれば、重量％で、 Ｃ：０．０５％以下、Ｓｉ：１．５％以下 Ｍｎ：１．０％以下、Ｃｒ：１１．０〜２６％ Ａｌ：１．０〜８．０％、Ｎ：０．０３％以下 Ｔｉ：０．０１〜２．０％、Ｚｒ：０．０１〜２．０％ Ｎｂ：０．０１〜１．５％、 Ｔｉ＋Ｚｒ＋Ｎｂの総量が、１．５％＜Ｔｉ＋Ｚｒ＋Ｎ
ｂ≦３．０％ ランタノイド：Ｃｅを０．０３％以下、その他のランタ
ノイド０．００１〜０．０５％の範囲内でかつランタノ
イドの合計が０．０５〜０．２％を含み、残部Ｆｅおよ
び不可避的不純物からなることを特徴とするろう付け後
の高温強度および耐酸化性に優れたＦｅ−Ｃｒ−Ａｌ系
合金が提供される。According to the fourth aspect of the present invention, in% by weight, C: 0.05% or less, Si: 1.5% or less, Mn: 1.0% or less, Cr: 11.0 to 26% Al. : 1.0 to 8.0%, N: 0.03% or less Ti: 0.01 to 2.0%, Zr: 0.01 to 2.0% Nb: 0.01 to 1.5%, Ti + Zr + Nb Is 1.5% <Ti + Zr + N
b ≦ 3.0% Lanthanoid: Ce of 0.03% or less, other lanthanoids within the range of 0.001 to 0.05%, and the total of lanthanoids including 0.05 to 0.2%, and the balance Fe and Provided is an Fe-Cr-Al-based alloy excellent in high-temperature strength and oxidation resistance after brazing, which is characterized by comprising unavoidable impurities.
【０００９】[0009]
【作用】以下に本発明をさらに詳細に説明する。本発明
のＦｅ−Ｃｒ−Ａｌ合金は四態様があり、基本的には、
Ｃ，Ｓｉ，Ｍｎ，Ｃｒ，Ａｌ，Ｎを含有する。それ以外
に下記の２つのグループの組合せの元素を含有する。下
記（１−１）、（１−２）、（２−１）および（２−
２）の組合せにより、ろう付け後の高温強度および耐酸
化性を改善することができる。その用途は特に合金板ま
たは箔として、自動車などの触媒コンバータ用材料をは
じめとした耐熱材料に好適である。 （１）Ｔｉ，Ｚｒ，Ｎｂ （１−１）ＴｉおよびＺｒを含有する場合は、Ｔｉ＋Ｚ
ｒは１．５〜３％とする。 （１−２）また、これらに加えてＮｂを含有する場合
は、Ｔｉ＋Ｚｒ＋Ｎｂは１．５〜３％とする。 （２）ランタノイド （２−１）ランタノイドの内Ｌａを含有する場合は０．
０５〜０．２％とする。 （２−２）Ｃｅを除くランタノイドを含有する場合は
０．００１〜０．０５％かつその合計量は０．０５〜
０．２％とする。 （２−１）および（２−２）のいずれの場合にも、Ｃｅ
は０．０３％以下とする。The present invention will be described in more detail below. The Fe-Cr-Al alloy of the present invention has four modes, and basically,
It contains C, Si, Mn, Cr, Al, N. In addition, it contains elements of the following two groups in combination. The following (1-1), (1-2), (2-1) and (2-
The combination of 2) can improve the high temperature strength and the oxidation resistance after brazing. Its application is particularly suitable as a heat-resistant material such as an alloy plate or a foil, such as a material for a catalytic converter for automobiles. (1) Ti, Zr, Nb (1-1) When Ti and Zr are contained, Ti + Z
r is 1.5 to 3%. (1-2) When Nb is contained in addition to these, Ti + Zr + Nb is set to 1.5 to 3%. (2) Lanthanoid (2-1) When La is contained in the lanthanoid, it is 0.
05 to 0.2%. (2-2) When containing lanthanoids other than Ce, 0.001 to 0.05% and the total amount thereof is 0.05 to
0.2%. In both cases of (2-1) and (2-2), Ce
Is 0.03% or less.
【００１０】次に本発明合金の各成分の限定理由につい
て述べる。なお、下限がないものについては０％を含
む。 Ａｌ：Ａｌは本発明において耐酸化性およびクリープ強
度を確保するために、不可欠な元素であり、Ｆｅ−Ｃｒ
−Ａｌ合金を高温に保持した場合、ＡｌはＦｅ−Ｃｒよ
り優先酸化されて合金表面に保護性の高いＡｌ2 Ｏ3 皮
膜を生成し、耐酸化性を改善する。Ａｌ含有量が１．０
％未満であると耐酸化性およびクリープ強度に優れたＡ
ｌ2 Ｏ3 皮膜が生成しないため、その下限を１．０％以
上に限定する。耐酸化性およびクリープ特性の点からは
Ａｌ含有量を高めることが望ましいが、一方でＡｌは８
％を越えると熱間圧延が困難なのでその上限を８％以下
に限定する。Next, the reasons for limiting each component of the alloy of the present invention will be described. In addition, 0% is included when there is no lower limit. Al: Al is an indispensable element for ensuring the oxidation resistance and the creep strength in the present invention.
When holding the -Al alloy to a high temperature, Al will be preferentially oxidized than Fe-Cr generates a high Al 2 O 3 film having protective properties to the alloy surface, improves the oxidation resistance. Al content is 1.0
% Is less than A, which is excellent in oxidation resistance and creep strength.
Since the l 2 O 3 film is not formed, the lower limit is limited to 1.0% or more. From the viewpoint of oxidation resistance and creep properties, it is desirable to increase the Al content, while Al is 8
%, Hot rolling is difficult, so the upper limit is limited to 8% or less.
【００１１】Ｃｒ：ＣｒはＡｌの耐酸化性を向上させる
役割を持つばかりではなく、Ｃｒ自体が耐酸化性を向上
させる元素である。ここで１１％未満では耐酸化性が確
保できず、２６％を越えると靭性が低下し冷間圧延が困
難となるので１１％以上２６％以下とした。Cr: Cr not only has the role of improving the oxidation resistance of Al, but Cr itself is an element that improves the oxidation resistance. Here, if it is less than 11%, the oxidation resistance cannot be secured, and if it exceeds 26%, the toughness deteriorates and cold rolling becomes difficult, so the content was made 11% or more and 26% or less.
【００１２】Ｓｉ：ＳｉはＡｌ同様耐酸化性を高める元
素であるが多量に含有すると靭性を低下させ製造性を低
下させるのでその上限を１．５％以下に限定する。Si: Si is an element that enhances the oxidation resistance like Al, but if it is contained in a large amount, it lowers the toughness and the manufacturability, so its upper limit is limited to 1.5% or less.
【００１３】Ｍｎ：ＭｎはＡｌ脱酸の予備材として添加
される場合、鋼中に残存することがあるが、Ｍｎは耐酸
化性および耐食性を劣化させるので、少ない方がよい。
工業的および経済的な溶製技術を考慮して１．０％以下
に限定した。Mn: Mn may remain in the steel when added as a preliminary material for deoxidation of Al, but Mn deteriorates the oxidation resistance and the corrosion resistance, so its content is preferably small.
It was limited to 1.0% or less in consideration of industrial and economical melting technology.
【００１４】Ｌａ：ＬａはＦｅ−Ｃｒ−Ａｌ合金におい
て高温で生成するＡｌ2 Ｏ3 ，Ｃｒ 2 Ｏ3 等の酸化皮膜
の密着性を改善し、耐酸化性および酸化スケールの耐剥
離性向上に極めて顕著な効果を有する。酸化スケールの
剥離防止は耐酸化性の向上のみならず、箔でのクリープ
強度に、酸化皮膜の強度をも加算するので極めて重要な
元素である。この効果は、０．０５％未満では耐酸化特
性、クリープ特性を確保できず、０．２％以上では熱間
圧延が不可能となるので、０．０５％以上０．２％以下
に限定する。La: La is an Fe-Cr-Al alloy
Al generated at high temperature2O3, Cr 2O3Oxide film
To improve the adhesiveness of the oxide, and to prevent oxidation and peeling of oxide scale.
It has a very remarkable effect in improving releasability. Oxide scale
Peeling prevention not only improves oxidation resistance but also creep in foil
It is extremely important because the strength of the oxide film is added to the strength.
It is an element. If this effect is less than 0.05%, the oxidation resistance is
Resistance and creep characteristics cannot be ensured, and if 0.2% or more, hot
Since rolling becomes impossible, 0.05% or more and 0.2% or less
Limited to
【００１５】Ｃｅを除くランタノイド：Ｃｅを除くラン
タノイドはＦｅ−Ｃｒ−Ａｌ系合金に対しＬａと同様に
高温で生成する酸化皮膜の密着性を向上することを通じ
て耐酸化性を向上する効果を有し、かつ、源鉱石からＬ
ａを生成する場合、純粋なＬａよりＮｄなど含有した場
合の方が容易な場合があることから、Ｃｅを除くランタ
ノイドを０．００１〜０．０５％の範囲で含有させるこ
とができる。それに多量に添加すると熱間圧延が不可能
となるのでランタノイドの合計は０．２％以下とする。Lanthanoids other than Ce: Lanthanides other than Ce have the effect of improving the oxidation resistance by improving the adhesion of the oxide film formed at high temperature to Fe-Cr-Al alloys, like La. , And from the source ore to L
When a is produced, it may be easier to contain Nd or the like than pure La. Therefore, the lanthanoid excluding Ce can be contained in the range of 0.001 to 0.05%. If a large amount is added to it, hot rolling becomes impossible, so the total content of lanthanoids should be 0.2% or less.
【００１６】Ｃｅ：希土類を添加する際にミッシュメタ
ルで添加すると経済的であるが、Ｃｅの添加は避けられ
ない。Ｃｅは熱間加工性および耐酸化性を劣化させるの
で添加しないほうが好ましいが、０．０３％以下では特
性上、製造上問題がない。よって添加の上限を０．０３
％以下に限定する。Ce: It is economical to add a rare earth element with a misch metal, but addition of Ce is unavoidable. Since Ce deteriorates the hot workability and the oxidation resistance, it is preferable not to add Ce, but if it is 0.03% or less, there is no problem in manufacturing due to the characteristics. Therefore, the upper limit of addition is 0.03
% Or less.
【００１７】Ｚｒ：ＺｒＮ，ＺｒＣを生成し高温強度を
高める効果がある。また、Ｚｒは表面濃化してＺｒＯ2
の酸化物を生成する。ＺｒはＬａと複合で含有する場合
にＡｌの酸化消耗を抑制しＡｌ2 Ｏ3 皮膜およびＣｒ2
Ｏ3 皮膜を形成する時間を延ばし、合金の耐酸化性を向
上させる。この効果は０．０１％以上で顕著となる。強
度の点からは、Ｚｒはできるだけ多く添加するのが望ま
しいが、その含有量が２．０％を越えると耐酸化性が低
下するので、その含有量を０．０１％以上２．０％以下
とした。Zr: ZrN and ZrC are produced, which has the effect of increasing the high temperature strength. In addition, Zr is concentrated on the surface to produce ZrO 2
Produces oxides of. Zr suppresses the oxidative consumption of Al when it is contained in combination with La and suppresses Al 2 O 3 coating and Cr 2
Extends the time for forming an O 3 film and improves the oxidation resistance of the alloy. This effect becomes remarkable at 0.01% or more. From the viewpoint of strength, it is desirable to add Zr as much as possible, but if the content exceeds 2.0%, the oxidation resistance will decrease, so the content should be 0.01% or more and 2.0% or less. And
【００１８】Ｔｉ：ＴｉはＺｒ同様ＴｉＮ，ＴｉＣを生
成し高温強度を高める効果がある。この効果は０．０１
％以上添加しないと効果がないのでその下限を０．０１
％以上とする。また過剰に添加すると耐酸化性が低下す
るのでその上限を２．０％に限定する。ＴｉとＺｒが共
存するときは、Ｔｉ＋Ｚｒは１．５〜３．０％とする。
それは、１．５％未満ではろう接後のクリープ特性に劣
り、３％を超えると耐酸化性が低下するためである。Ti: Ti, like Zr, produces TiN and TiC and has the effect of increasing the high temperature strength. This effect is 0.01
% Is not effective, so the lower limit is 0.01
% Or more. Further, if added excessively, the oxidation resistance is lowered, so the upper limit is limited to 2.0%. When Ti and Zr coexist, Ti + Zr is 1.5 to 3.0%.
This is because if it is less than 1.5%, the creep property after brazing is inferior, and if it exceeds 3%, the oxidation resistance is lowered.
【００１９】Ｎｂ：ＮｂもＺｒ，Ｔｉ同様、ＮｂＣ，Ｎ
ｂＮを生成し高温強度を高める効果がある。この効果は
０．０１％以上添加しないと効果がないのでその下限を
０．０１％とする。また、過剰に添加すると耐酸化性が
低下するのでその上限を２．０％に限定する。 Ｔｉお
よびＺｒと共存するときは、Ｔｉ＋Ｚｒ＋Ｎｂは１．５
〜３％とする。１．５％未満ではろう接後のクリープ特
性に劣り、３％を超えると耐酸化性が低下するためであ
る。Nb: Nb is also NbC, N, like Zr and Ti.
It has the effect of generating bN and increasing the high temperature strength. This effect is not effective unless added in an amount of 0.01% or more, so the lower limit is made 0.01%. Further, if added excessively, the oxidation resistance is lowered, so its upper limit is limited to 2.0%. When coexisting with Ti and Zr, Ti + Zr + Nb is 1.5
~ 3%. This is because if it is less than 1.5%, the creep property after brazing is inferior, and if it exceeds 3%, the oxidation resistance decreases.
【００２０】Ｃ：Ｃは過剰になると高温強度および耐酸
化性さらに靭性を低下させるので、極力低減させる方が
望ましい。よって０．０５％以下に限定する。C: If C is excessive, the high temperature strength, the oxidation resistance and the toughness are lowered, so it is desirable to reduce it as much as possible. Therefore, it is limited to 0.05% or less.
【００２１】Ｎ：Ｎは微細な炭化物の生成元素であるＺ
ｒ，Ｔｉ，ＮｂなどをＮ化物として固定してしまい、粗
大なＣｒ，Ｆｅの炭化物が析出して高温での強度を低下
するので極力低減させることが望ましい。また、Ｎが過
剰になると靭性を低下させ、また、冷間圧延性、加工性
を低下させる。Ａｌと反応し、粗大なＡｌＮ（〜１０μ
ｍ）を析出すると５０μｍ程度の箔に圧延した場合、穴
開きの原因にもなる。よって０．０３％以下に限定す
る。N: N is a fine carbide forming element Z
Since r, Ti, Nb, etc. are fixed as N-oxides and coarse Cr and Fe carbides precipitate to lower the strength at high temperature, it is desirable to reduce them as much as possible. Further, when N is excessive, toughness is lowered, and cold rolling property and workability are also deteriorated. Coarse AlN (~ 10μ reacts with Al
When m) is deposited, it also causes holes when rolled into a foil of about 50 μm. Therefore, it is limited to 0.03% or less.
【００２２】[0022]
【実施例】以下に本発明を実施例に基づいて具体的に説
明する。 （実施例）表１に本発明例および比較例の化学組成を示
す。これら素材は真空溶解によって溶製され、１２５０
℃に加熱後、板厚３ｍｍまで熱間圧延し、焼鈍と冷間圧
延を繰り返し５０μｍの箔にした。この圧延箔をＮｉろ
う材を用いて１２００℃で真空ろう付けを行った後、耐
酸化性の調査をした。その結果を同様に表１に示す。１
２００℃，１５０ｈの酸化で酸化増量が１．５ｍｇ／ｃ
ｍ2 未満のものを○で、これ以上のものを×で示した。
また、高温強度の評価は、５０μｍの冷延箔を用いて、
８００℃、大気中、初期応力３ｋｇｆ／ｍｍ2 を負荷し
たクリープ試験により行った。破断時間が８ｈ以上のも
のを○印で、これ未満のものを×で示した。本発明鋼１
〜７までは耐酸化性およびクリープ強度に優れている。
一方、比較鋼８〜１１は耐酸化性は優れるが、クリープ
特性に劣り、比較鋼１２はクリープ特性には優れるが耐
酸化特性には劣る。また、比較鋼１３〜１５は耐酸化性
およびクリープ特性いずれの特性にも劣る。EXAMPLES The present invention will be specifically described below based on examples. (Example) Table 1 shows the chemical compositions of the present invention and comparative examples. These materials are melted by vacuum melting, 1250
After heating to 0 ° C., hot rolling was performed to a plate thickness of 3 mm, and annealing and cold rolling were repeated to obtain a foil of 50 μm. The rolled foil was vacuum brazed at 1200 ° C. using a Ni brazing material, and then the oxidation resistance was investigated. The results are also shown in Table 1. 1
Oxidation increase of 1.5mg / c by oxidation at 200 ℃ for 150h
Those having a size of less than m 2 are shown by ◯, and those having a size of more than m 2 are shown by x.
Further, the evaluation of the high temperature strength was performed by using a cold rolled foil of 50 μm,
The creep test was carried out at 800 ° C. in the atmosphere with an initial stress of 3 kgf / mm 2 . Those with a breaking time of 8 hours or more are shown by ◯, and those with a breaking time of less than 8 h are shown by x. Invention Steel 1
Up to 7 are excellent in oxidation resistance and creep strength.
On the other hand, Comparative Steels 8 to 11 are excellent in oxidation resistance but inferior in creep property, and Comparative Steel 12 is excellent in creep property but inferior in oxidation resistance property. Further, Comparative Steels 13 to 15 are inferior in both the oxidation resistance and the creep characteristics.
【００２３】[0023]
【表１】 [Table 1]
【００２４】[0024]
【発明の効果】本発明は、Ｆｅ−Ｃｒ−Ａｌ系合金にＴ
ｉとＺｒあるいはさらにＮｂを複合添加し、またＬａあ
るいはランタノイドを含有することにより、高温強度お
よび耐酸化性に優れた合金を提供できる。本発明の合金
板またその箔は自動車などの触媒コンバータ用材料をは
じめとした、耐熱材料として好適な合金であり、とくに
板厚０．１ｍｍ以下の箔として優れた性能を示す。INDUSTRIAL APPLICABILITY The present invention is applicable to Fe-Cr-Al alloys with T
An alloy excellent in high temperature strength and oxidation resistance can be provided by adding i and Zr or further Nb in combination and by containing La or lanthanoid. The alloy sheet or the foil thereof according to the present invention is an alloy suitable as a heat-resistant material including materials for catalytic converters for automobiles and the like, and particularly exhibits excellent performance as a foil having a sheet thickness of 0.1 mm or less.
Claims (4)
を満たし、 Ｌａ：０．０５〜０．２％、Ｃｅ：０．０３％以下を含
み、残部Ｆｅおよび不可避的不純物からなることを特徴
とするろう付け後の高温強度および耐酸化性に優れたＦ
ｅ−Ｃｒ−Ａｌ系合金。1. By weight%, C: 0.05% or less, Si: 1.5% or less, Mn: 1.0% or less, Cr: 11.0 to 26%, Al: 1.0 to 8.0%. , N: 0.03% or less Ti: 0.01 to 2.0%, Zr: 0.01 to 2.0% The total amount of Ti + Zr is 1.5% <Ti + Zr ≦ 3.0%.
And La: 0.05 to 0.2%, Ce: 0.03% or less, and the balance Fe and unavoidable impurities, and is excellent in high-temperature strength and oxidation resistance after brazing. F
e-Cr-Al alloy.
ノイド０．００１〜０．０５％の範囲内でかつランタノ
イドの合計が０．０５〜０．２％を含み、残部Ｆｅおよ
び不可避的不純物からなることを特徴とするろう付け後
の高温強度および耐酸化性に優れたＦｅ−Ｃｒ−Ａｌ系
合金。2. In% by weight, C: 0.05% or less, Si: 1.5% or less, Mn: 1.0% or less, Cr: 11.0 to 26% Al: 1.0 to 8.0% , N: 0.03% or less Ti: 0.01 to 2.0%, Zr: 0.01 to 2.0% The total amount of Ti + Zr is 1.5% <Ti + Zr ≦ 3.0%. Lanthanoid: Ce is 0. 0.03% or less, other lanthanoids within the range of 0.001 to 0.05%, and the total amount of lanthanoids includes 0.05 to 0.2%, and the balance is Fe and inevitable impurities. Fe-Cr-Al based alloy excellent in high temperature strength and oxidation resistance after attachment.
ｂ≦３．０％を満たし、 Ｌａ：０．０５〜０．２％、Ｃｅ：０．０３％以下を含
み、残部Ｆｅおよび不可避的不純物からなることを特徴
とするろう付け後の高温強度および耐酸化性に優れたＦ
ｅ−Ｃｒ−Ａｌ系合金。3. By weight%, C: 0.05% or less, Si: 1.5% or less, Mn: 1.0% or less, Cr: 11.0 to 26% Al: 1.0 to 8.0% , N: 0.03% or less Ti: 0.01 to 2.0%, Zr: 0.01 to 2.0% Nb: 0.01 to 1.5%, the total amount of Ti + Zr + Nb is 1.5% < Ti + Zr + N
b ≦ 3.0%, La: 0.05 to 0.2%, Ce: 0.03% or less, and the balance Fe and inevitable impurities at high temperature strength after brazing and F with excellent oxidation resistance
e-Cr-Al alloy.
ｂ≦３．０％ ランタノイド：Ｃｅを０．０３％以下、その他のランタ
ノイド０．００１〜０．０５％の範囲内でかつランタノ
イドの合計が０．０５〜０．２％を含み、残部Ｆｅおよ
び不可避的不純物からなることを特徴とするろう付け後
の高温強度および耐酸化性に優れたＦｅ−Ｃｒ−Ａｌ系
合金。4. By weight%, C: 0.05% or less, Si: 1.5% or less, Mn: 1.0% or less, Cr: 11.0 to 26% Al: 1.0 to 8.0% , N: 0.03% or less Ti: 0.01 to 2.0%, Zr: 0.01 to 2.0% Nb: 0.01 to 1.5%, the total amount of Ti + Zr + Nb is 1.5% < Ti + Zr + N
b ≦ 3.0% Lanthanoid: Ce of 0.03% or less, other lanthanoids within the range of 0.001 to 0.05%, and the total of lanthanoids including 0.05 to 0.2%, and the balance Fe and An Fe-Cr-Al-based alloy excellent in high-temperature strength and oxidation resistance after brazing, which is characterized by comprising unavoidable impurities.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP11809993A JPH06330246A (en) | 1993-05-20 | 1993-05-20 | Fe-cr-al alloy excellent in high temperature strength after brazing and oxidation resistance |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP11809993A JPH06330246A (en) | 1993-05-20 | 1993-05-20 | Fe-cr-al alloy excellent in high temperature strength after brazing and oxidation resistance |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH06330246A true JPH06330246A (en) | 1994-11-29 |
Family
ID=14727985
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP11809993A Withdrawn JPH06330246A (en) | 1993-05-20 | 1993-05-20 | Fe-cr-al alloy excellent in high temperature strength after brazing and oxidation resistance |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH06330246A (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US7005105B2 (en) * | 2000-12-28 | 2006-02-28 | Korea Electrotechnology Research Institute | Fe-Cr-Al alloys for electric resistance wires |
-
1993
- 1993-05-20 JP JP11809993A patent/JPH06330246A/en not_active Withdrawn
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US7005105B2 (en) * | 2000-12-28 | 2006-02-28 | Korea Electrotechnology Research Institute | Fe-Cr-Al alloys for electric resistance wires |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| JP3474829B2 (en) | Heat-resistant ferritic stainless steel for catalyst support with excellent weldability and workability | |
| US9273382B2 (en) | Stainless steel foil and catalyst carrier for exhaust gas purifying device using the foil | |
| JPS63266044A (en) | High al rolled metallic foil for catalyst carrier | |
| JP3247162B2 (en) | Fe-Cr-Al-based alloy excellent in oxidation resistance and foil thereof | |
| JP3335647B2 (en) | Fe-Cr-Al alloy excellent in durability and catalyst carrier using the same | |
| JP3320831B2 (en) | Fe-Cr-Al alloy with excellent high temperature strength and oxidation resistance | |
| JPH06212363A (en) | Fe-cr-al series alloy steel excellent in high temperature oxidation resistance and high temperature durability | |
| WO2002002836A1 (en) | Fe-cr-al based alloy foil and method for producing the same | |
| JP2003105506A (en) | Fe-Cr-Al BASED ALLOY FOIL HAVING EXCELLENT OXIDATION RESISTANCE AND HIGH TEMPERATURE DEFORMATION RESISTANCE, AND PRODUCTION METHOD THEREFOR | |
| JP3200160B2 (en) | Fe-Cr-Al alloy excellent in oxidation resistance and high-temperature embrittlement resistance, catalyst carrier using the same, and method for producing alloy foil | |
| JPH06330246A (en) | Fe-cr-al alloy excellent in high temperature strength after brazing and oxidation resistance | |
| JP2002507249A (en) | Ferritic stainless steel and its use as a substrate for catalytic converters | |
| JPH0672287B2 (en) | Heat-resistant ferritic stainless steel foil with excellent acid resistance in combustion exhaust gas | |
| JP3351837B2 (en) | Al-containing ferritic stainless steel with excellent manufacturability and high-temperature oxidation resistance | |
| JP3283286B2 (en) | Fe-Cr-Al alloy foil for highly heat-resistant metal carrier for automobile exhaust gas purification catalyst | |
| JP2885497B2 (en) | High-temperature, high-strength, high-heat-resistant Fe-Cr-Al engaging gold with excellent manufacturability | |
| JPH08269730A (en) | Fe-cr-al alloy plate having excellent oxidation resistance | |
| JP2004269915A (en) | Al-CONTAINING HIGHLY OXIDATION RESISTANT STAINLESS STEEL FOIL HAVING NO WRINKLING ON JOINING, AND CATALYST CARRIER | |
| JPH06220587A (en) | Fe-cr-al alloy excellent in oxidation resistance and minimal in electric resistance reduction rate | |
| JP2002105606A (en) | Fe-Cr-Al BASED ALLOY | |
| JPH05277380A (en) | Fe-cr-al alloy foil for highly heat-resistant automobile exhaust gas purifying catalyst metal carrier | |
| JP3142884B2 (en) | Fe-Cr-Al alloy that has excellent catalyst peeling resistance and suppresses whisker formation that reduces the adhesion of γAl2O3 | |
| JP3491334B2 (en) | Fe-Cr-Al alloy for catalytic converter carrier excellent in oxidation resistance and method for producing alloy foil using the same | |
| JPH0953156A (en) | Iron-chrome-alum. alloy foil for electrothermal catalyst | |
| JP2004285393A (en) | Heat resistant material |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| A300 | Withdrawal of application because of no request for examination |
Free format text: JAPANESE INTERMEDIATE CODE: A300 Effective date: 20000801 |