JPS6289811A - Manufacture of high-cr ferritic steel having high strength - Google Patents
Manufacture of high-cr ferritic steel having high strengthInfo
- Publication number
- JPS6289811A JPS6289811A JP22699485A JP22699485A JPS6289811A JP S6289811 A JPS6289811 A JP S6289811A JP 22699485 A JP22699485 A JP 22699485A JP 22699485 A JP22699485 A JP 22699485A JP S6289811 A JPS6289811 A JP S6289811A
- Authority
- JP
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- Prior art keywords
- strength
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- steel
- temperature
- transformation point
- Prior art date
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Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Heat Treatment Of Steel (AREA)
- Heat Treatment Of Articles (AREA)
Abstract
Description
【発明の詳細な説明】
（産業上の利用分野）
本発明は高Ｃｒ フェライト鋼の高温長時間側のクリ
ープ強度を改良するための熱処理方法に関する。DETAILED DESCRIPTION OF THE INVENTION (Field of Industrial Application) The present invention relates to a heat treatment method for improving the creep strength of high Cr ferritic steel at high temperatures and long periods of time.
（従来の技術） 高Ｃｒ フェライト鋼は低合金鋼に比べ、強度。(Conventional technology) High Cr ferritic steel is stronger than low alloy steel.
耐食性が優れ、ステンレス鋼の欠点である応力腐食割れ
を起さないこと、熱伝導率が高い材料であることがらボ
イラ、原子力、化学工業用の耐熱材料として広く利用さ
れている。中でも、Ｖ 、 Ｎｂ などの析出強化元
；＋−′ｆ！：含む高Ｃｒ ７エライト鋼は高温クリ
ープ強度が改善され、６００Ｃ以下の温度ではＳ Ｕ
Ｓ ５０４Ｈ鋼の強度を上層る。こうした析出強化型窩
Ｃｒ フェライト鋼としてはもともとタービン用材料
として開発された１ ２ Ｃｉｒ −Ｉ Ｍｏ鋼（Ｘ
２０ ＣｒＭｏＶ １２１ ）、ボイラあるいは熱交換
器用として開発された改良９ Ｃｒ −Ｉ Ｍｏ鋼（Ａ
ＳＴＭ Ａ ２１ ｓ Ｔ９１ ）、本発明者らが開発
した９〜１２ｃｒ 鋼（特公昭５７−５６５ａ１、特開
昭５８−１８１８４９）がある。It is widely used as a heat-resistant material for boilers, nuclear power, and chemical industries because it has excellent corrosion resistance, does not cause stress corrosion cracking, which is a disadvantage of stainless steel, and has high thermal conductivity. Among them, precipitation strengthening elements such as V and Nb; +-'f! : High Cr 7 elite steel has improved high temperature creep strength, and S U at temperatures below 600C.
Superior strength to S504H steel. Among these precipitation-strengthened cavity Cr ferritic steels is 12Cir-I Mo steel (X
20 CrMoV 121), modified 9 Cr-I Mo steel (A
STM A 21s T91) and 9 to 12 cr steel developed by the present inventors (Japanese Patent Publication No. 57-565a1, Japanese Unexamined Patent Publication No. 58-181849).
ところで、析出強化型窩Ｃｒ フェライト鋼は５８０
Ｃ以下の温度では１０ｈの長時間側においても高いクリ
ープ強度を有するものの、６００Ｃ以上の高温になると
クリープ中に組織変化を伴なった強度の急低下を生ず、
る場合があることが報告されている。これはＶ 、 Ｎ
ｂ を含む析出強化鋼の高温クリープ中の微細析出物
の成長に関連し、マルテンサイト組織の回復後、再結晶
の組織変化に起因すると考えられる。By the way, precipitation strengthened cavity Cr ferritic steel is 580
At temperatures below C, it has high creep strength even over long periods of 10 hours, but at temperatures above 600 C, there is a sudden decrease in strength accompanied by structural changes during creep.
It has been reported that there may be cases where This is V, N
It is considered to be related to the growth of fine precipitates during high-temperature creep of precipitation-strengthened steel containing b, and is caused by the structural change of recrystallization after recovery of the martensitic structure.
このような問題に対して、従来から１ｈ以上の長時関節
なまし処理ｔ−ｍすことによって、組織を安定化できる
ことは知られてい喪。しかし。Regarding such problems, it has not been known that the tissue can be stabilized by long-term joint annealing treatment for 1 hour or more. but.
従来社ムＣ１変態点′ｆｃ８Ａ確にした成分設計は全く
行なわれていなかったため焼戻し温度は８００Ｃ以下に
設定されていた。発明者らの検討結果ではＶ 、 Ｎｂ
添加高ｃｒ ｍを８００Ｃ以下の温度で焼戻して使
用する場合、６００Ｃ以上の高温クリープ試験中に長時
間鯛で強度が急に低下する場合が多いことが明らかにな
った。In the past, the tempering temperature was set at 800C or lower because no precise component design had been carried out. According to the inventors' study results, V, Nb
It has become clear that when the added crm is tempered at a temperature of 800C or lower, the strength of sea bream suddenly decreases in many cases for a long time during a high-temperature creep test of 600C or higher.
（発明が解決しようとする問題点）
本発明は、Ｖ、 Ｎｂを単独もしくは複合して含む高Ｃ
ｒ ’フェライト系耐熱鋼について高温長時間側のクリ
ープ強ｇを改善するための熱処理法に関連した高強度高
Ｃｒ フェライト鋼の製造方法を提供しようとするも
のである。(Problems to be Solved by the Invention) The present invention solves the problem of high C
It is an object of the present invention to provide a method for producing high-strength, high-Cr ferritic steel related to a heat treatment method for improving the creep strength g on the high-temperature, long-term side of r' ferritic heat-resistant steel.
（問題点を解決するための手段）
本発明は、成分Ｎ量へとし、ｃ ： ０．２％以）Ｓｉ
：１％以下、Ｍｎ ： ０．１〜１．５％、Ｐ ： ０
．０５％以下、ｓ：ｏ、ｏ３％以下、Ｎｉ：１％以下。(Means for Solving the Problems) The present invention reduces the amount of component N, c: 0.2% or more) Si
: 1% or less, Mn: 0.1-1.5%, P: 0
．． 05% or less, s: o, o3% or less, Ni: 1% or less.
Ｃｒ：５〜１５％、 Ｍｏ ： ０．０２〜５％、Ｗ：
４％以下、ＳｏＩ！＾ｚ ： ｏ、ｏ ｎ％以）、Ｎ：
０．０７％以下であッテ、ｖ ： ｏ、ｏ １〜０．４
およびＮｂ：０．０１〜０．３％を単独又は複合して含
有し、かつＡｃｌが８２０Ｃ以上である鋼について、
Ａｃ３以上の温度で焼ならし後、８１０Ｃ以上かつＡＣ
ｔ以下の温度で焼もとし処理することにより高温長時間
クリープ強度を改善する方法である。Cr: 5-15%, Mo: 0.02-5%, W:
Less than 4%, SoI! ^z: o, on% or more), N:
0.07% or less, v: o, o 1 to 0.4
and Nb: For steel containing 0.01 to 0.3% alone or in combination and having ACl of 820C or more,
After normalizing at a temperature of Ac3 or higher, 810C or higher and AC
This is a method of improving high-temperature long-term creep strength by performing annealing treatment at a temperature below t.
以下に、本発明の詳細な説明を行なう。本発明の特徴は
高Ｃｒ フェライト鋼のＡＣ１変態点を明確にした式
、すなわち。A detailed explanation of the present invention is given below. The feature of the present invention is a formula that clarifies the AC1 transformation point of high Cr ferritic steel.
Ａｃ１ （ｃ’）＝＝ ７６５−５０００−４５０ Ｎ
＋３０Ｓｉ−２５Ｍｎ ＋２５ Ｍｏ ＋１５ Ｗ ＋
１１Ｃｒ＋５０ Ｖ＋３０ Ｎｂ−３０Ｎｉ十ａＯＡＺ
（単位１重量％）
の式（ＩＪの導入によりＡＯｌが８２０Ｃ以上の成分系
を選定し、かつ従来全く行なわれていなかった８１０Ｃ
以上ＡＣ１以下の高温焼戻しを抱すことによって、組織
を安定化し、６０ＱＣ以上の為温良時間クリープ強度の
低下を防止して、強度を改善できることを見出した点に
ある。Ac1 (c') = = 765-5000-450 N
+30Si-25Mn +25 Mo +15 W +
11Cr+50 V+30 Nb-30Ni 10aOAZ
(Unit: 1% by weight) The formula (by introducing IJ, we selected a component system with AOl of 820C or higher, and 810C, which had never been done before)
It has been found that by subjecting the steel to high-temperature tempering of AC1 or less, the structure can be stabilized, and since the temperature is 60QC or higher, a decrease in the creep strength during warm hours can be prevented and the strength can be improved.
以下、成分限定理由を以下に示す。The reasons for limiting the ingredients are shown below.
ｃ ： ０．２％を超える場合、ムｃ１が低下し、８１
０Ｃ以上の高温焼戻しが不可能になる。また、加工性、
溶接性も著しく損われる。従って、ｃｌ−は０．２％以
下とした。c: If it exceeds 0.2%, mu c1 decreases and 81
Tempering at a high temperature of 0C or higher becomes impossible. In addition, processability,
Weldability is also significantly impaired. Therefore, Cl- was set to 0.2% or less.
Ｃｒ：高Ｃｒ フェライト系耐熱鋼として、十分な耐
食性、耐電化性を付与するためには５％以上のＣｒ 添
加が必要である。また、Ｃｒｔ＆が１５％を超えると一
一フエライト童が著しく増え１強度を損う。従って、５
〜１５％とした。Cr: High Cr As a ferritic heat-resistant steel, it is necessary to add 5% or more of Cr in order to provide sufficient corrosion resistance and electrical resistance. Moreover, when Crt & exceeds 15%, the number of 11 ferrites increases significantly and the strength is impaired. Therefore, 5
~15%.
Ｖ：析出強化元素とし゛（０，０１％以上の添加が必要
であるが、０．４％を超える添加は析出強化に寄与する
Ｖが少なく、かえって強度を損う。V: Precipitation strengthening element (it is necessary to add 0.01% or more, but if it exceeds 0.4%, there will be less V contributing to precipitation strengthening, and the strength will be impaired instead.
従って、０．０１〜０．４％とした。Therefore, it was set at 0.01 to 0.4%.
Ｎｂ：析出強化元素として０．０１％以上のふたが必要
であるが、０．３％を超える添加は焼ならし処理時の未
固溶ＮｂＣが増え１強度を損う。従って、０．０１〜０
．３％とした。Nb: As a precipitation strengthening element, 0.01% or more is required, but addition of more than 0.3% increases undissolved NbC during normalizing treatment and impairs strength. Therefore, 0.01~0
．． It was set at 3%.
Ｖ 、 Ｎｂ については必すしも複合添加されず。V and Nb are not necessarily added in combination.
それぞれ単独添加した場合にも本発明の効果が得られる
ことから、Ｖ、Ｎｂ の複合もしくけ単独添加とした
。Since the effects of the present invention can be obtained even when each is added singly, a combination of V and Nb was also added alone.
Ｓｉ：脱酸剤として添加されるが１％金超えて存在する
場合、靭性と強□度を損うため、１％以下とした。Si: Added as a deoxidizing agent, but if more than 1% gold is present, toughness and strength will be impaired, so the content was set to 1% or less.
Ｍｎ：加工性を付与するために添加されるか、０．１％
未満では効果がなく、１．５％を超えて添加される場合
、硬化相を生ずる。したがって０．１〜１．５％とした
。Mn: Added to give processability, 0.1%
If less than 1.5%, it is ineffective, and if added in excess of 1.5%, a hardened phase is produced. Therefore, it was set at 0.1 to 1.5%.
ｐ、ｓ：いずれも強度と靭性に有害な不純物元素であシ
、できるだけ低い方が望ましい。通常の精錬処理を考慮
して０．０６％以下とした。p, s: Both are impurity elements harmful to strength and toughness, and it is desirable that their content be as low as possible. Considering the normal refining process, it was set to 0.06% or less.
Ｎｉニオ−ステナイト生成元素であり、添加によりＡｃ
１点が著しく低下する。本発明ではＡｃｊが８２０２：
’以上の成分を選定する必要性から、上限を定め１％以
下とした。Ni is a niostenite-forming element, and when added, Ac
1 point drops significantly. In the present invention, Acj is 8202:
'Due to the need to select the above components, the upper limit was set at 1% or less.
Ｍｏ＝耐熱鋼に高温強度を付与する必須元素で主に地に
固溶して強化に寄与するが、一部は炭化物、金属間化合
物として析出し、クリープ強度を改善する。０．０２％
未満ではこの効果がなく、３％を超えると多量のδ−フ
ェライトを含む状態となシ強度と靭性を損う。したがっ
て０．０２〜３％とした。Mo=An essential element that imparts high-temperature strength to heat-resistant steel.It mainly dissolves in solid solution in the ground and contributes to strengthening, but some of it precipitates as carbides and intermetallic compounds and improves creep strength. 0.02%
If it is less than 3%, this effect will not be achieved, and if it exceeds 3%, it will contain a large amount of δ-ferrite, which will impair strength and toughness. Therefore, it was set at 0.02 to 3%.
ｗ ： Ｍｏ同様、固溶強化元素であるが、１ｉｌｏと
の複合添加による強度改善効果が大きい。しかし４％を
超えて添加されるとδ−フェライト量が多くなり１強度
及び加工性を損うことから４％以下とした。w: Like Mo, it is a solid solution strengthening element, but the combined addition with 1ilo has a large strength improving effect. However, if it is added in excess of 4%, the amount of δ-ferrite increases, impairing strength and workability, so it is set at 4% or less.
ｓｏｇ 、Ａｚ ：脱酸剤として添加されるか、０．０
４％を超える場合は高温強度を損う。したがって０．０
４％以下とした。sog, Az: added as a deoxidizer or 0.0
If it exceeds 4%, high temperature strength will be impaired. Therefore 0.0
It was set to 4% or less.
Ｎ ： Ｖ 、 Ｎｂ と炭化物ノをつくり、高温強
１ｙを改善する。しかし０．０７％を超える場合、Ａｃ
１点が著しく下が９．８１０Ｃ以上の高温焼もどしが不
可能となる。したがって０．０７％以下とした。N: Creates carbides with V and Nb to improve high temperature strength 1y. However, if it exceeds 0.07%, Ac
If the score is significantly lower than 1 point, high temperature tempering of 9.810C or higher becomes impossible. Therefore, it was set to 0.07% or less.
次に式（１）は本発明者らが得たＡＣ１変態点の実験式
で上記成分範囲の中でＡＣｌが８２０Ｃ以上の成分系ラ
ミ１４足するために用いる。Next, formula (1) is an experimental formula for the AC1 transformation point obtained by the present inventors, and is used to add 14 component-based laminations with ACl of 820C or higher within the above-mentioned component range.
本発明はＡｃ１≧８２０Ｃの成分を選定し。In the present invention, components with Ac1≧820C are selected.
８１０Ｃ以上の隅温焼戻しを行なうことにより、長時間
クリ−７強度を改善できることが特徴である。この理由
はＶ 、 Ｎｂ 添加鋼では焼ならし後に生成するマ
ルテンサイト組Ｗｔ焼戻し処理する際、Ｖ、Ｎｂ の
微細な炭窒化物が析出して転位の圓復を著しく抑制し、
比較的低温の焼戻し処理では高温での使用に対して、不
安定な組織となる。すなわち、Ｖ 、 Ｎｂ 添加鋼
は焼戻し軟化抵抗が大きく、通常の８００ｔ？以下の焼
戻し処理では６００Ｃ以上の高温クリープ中にマルテン
サイト組織の再結晶化に伴い、著しく強度が低下するこ
とがある。これに対ｔ７．６１０Ｃ以上の高温焼戻し処
理材はマルテンサイト組織？十分に安定化させ、高温ク
リープ中の褥結晶化を抑制し、６００Ｃ以上、 １０’
ｈ以上の高温長時ｍ１クリ一プ強度を改善できるのであ
る。A feature is that long-term Cree-7 strength can be improved by performing corner temperature tempering at 810C or higher. The reason for this is that in steels containing V and Nb, fine carbonitrides of V and Nb precipitate during the martensite Wt tempering process that is generated after normalization, and this significantly suppresses the recovery of dislocations.
Tempering at a relatively low temperature results in an unstable structure when used at high temperatures. In other words, V and Nb added steel has a high resistance to tempering and softening, and the normal 800t? In the following tempering treatment, the strength may drop significantly due to recrystallization of the martensitic structure during high-temperature creep at 600C or higher. On the other hand, does the high-temperature tempered material with t7.610C or higher have a martensitic structure? Sufficiently stabilizes and suppresses bed crystallization during high temperature creep, over 600C, 10'
This makes it possible to improve the m1 clip strength for long periods of time at high temperatures of h or more.
（実肩例） 第１表に供試鋼の化学成分を示す。(Actual shoulder example) Table 1 shows the chemical composition of the test steel.
これらの１を１５０ｋｙｊＩ空加熱炉で溶解し。These 1 were melted in a 150kyjI empty heating furnace.
インゴット１１１５０〜９５０Ｃで鍛造して、厚さ２０
ｍの板材とした。これらの板材を第２表に示すような熱
処理を施した。６５０ｔＺ’Ｘ１０４ｈクリ一プ破断強
度を併せて示した。これより不発Ｅ！ＡＫよシ高温長時
間側クリープ破断強度が改善されていることが明らかで
ある。Forged with ingot 11150~950C, thickness 20
It was made into a plate material of m. These plate materials were subjected to heat treatment as shown in Table 2. 650tZ'X104h clip rupture strength is also shown. More dud E than this! It is clear that the creep rupture strength on the long-term side at high temperatures is improved compared to AK.
熱処理後、板材肉厚中央部よりφ６龍ｘＧＬ３０朋の引
張試験片を採取して、クリープ破断試験に供した。第１
図に第１表Ｊ−の６００Ｃ及び６５０Ｃにおけるクリー
プ破断試験結果を示す。従来法〈よる焼戻し材は１０ｈ
強度が比較的論いものの長時間側で強度低下を起す。一
方、本発明法による高温焼戻し材はＩＱｈ以上でも安定
な強度を保ち、６００Ｃでは＋ｏｈ以上で、また６５０
Ｃでｆ″Ｕ３０００ｈＵ３０００ｈ以上来法を強度の面
から土建る。After the heat treatment, a tensile test piece of φ6 Dragon x GL30 was taken from the center of the thickness of the plate and subjected to a creep rupture test. 1st
The figure shows the creep rupture test results at 600C and 650C in Table 1 J-. Conventional method (10 hours for tempered material)
Although the strength is relatively low, the strength decreases over a long period of time. On the other hand, the high-temperature tempered material obtained by the method of the present invention maintains stable strength even at IQh or higher, and at 600C it maintains stable strength at +oh or higher and at 650C or higher.
At C, f''U3000hU3000h or more is used for conventional construction from the viewpoint of strength.
本発明法のオリ点を以下に列挙する。The key points of the method of the present invention are listed below.
（１＋ ボイラ、化学工業、原子力用耐熱鋼として巷
に６０００以上の高温使用に対して安定な強度を有する
材料を供与できる。(1+ We can provide a material that has stable strength for use at high temperatures of 6000 or more, which is commonly used as heat-resistant steel for boilers, chemical industries, and nuclear power.
（２１高温焼戻し処理を施すために、材料が比較的軟質
であり、曲は加工性が改善されるとともに、冷間加工性
も良好になる。(21) Because of the high-temperature tempering treatment, the material is relatively soft, and the workability of the curve is improved, as well as good cold workability.
（３） 高温長時間１１ｔＱでの弛度の急低下を防止
するためには高温焼戻しが有効であり、本発明ではＡｃ
１の高い材料に限定し゛（高温焼戻しを行なう。そのた
めに化学成分とＡＣｌの関係式を見出し、高温焼戻しが
可能な成分設計を行なえるようになった。(3) High-temperature tempering is effective in preventing a sudden decrease in slack at high temperatures and long hours of 11 tQ, and in the present invention, Ac
For this purpose, we found a relational expression between chemical components and ACl, and were able to design components that would allow high-temperature tempering.
第１図は本発明方法と従来法のクリープ破断時間を比較
対比して示した図表である。
復代理人 内 １） 明
復代理人 萩 原 亮 −
復代理人 安 西 篤 夫
手続補正書
昭和６１年 ２ 月 ４日FIG. 1 is a chart comparing and contrasting the creep rupture times of the method of the present invention and the conventional method. Sub-agents 1) Clearance agent Ryo Hagiwara - Sub-agent Atsuo Anzai Proceedings amendment document February 4, 1986
Claims (1)
熱鋼の高温長時間クリープ強度を改善する熱処理法にお
いて、成分重量％とし、Ｃ：０．２以下、Ｓｉ：１％以
下、Ｍｎ：０．１〜１．５％、Ｐ：０．０３％以下、Ｓ
：０．０３％以下、Ｎｉ：１％以下、Ｃｒ：５〜１５％
、Ｍｏ：０．０２〜３％、Ｗ：４％以下、ＳｏｌＡｌ：
０．０４％以下、Ｎ：０．０７％以下であつて、Ｖ：０
．０１〜０．４％およびＮｂ：０．０１〜０．３％を単
独又は複合して含有し、かつＡｃ＿１が８２０℃以上で
ある鋼について、Ａｃ＿３以上の温度で焼ならし後、８
１０℃以上かつＡｃ＿１以下の温度で焼もどし処理する
ことにより高温長時間クリープ強度を改善することを特
徴とする高強度高Ｃｒフェライト鋼の製造方法。In a heat treatment method for improving the high-temperature long-term creep strength of high-Cr ferritic heat-resistant steel containing V and Nb alone or in combination, the components are expressed as % by weight, C: 0.2 or less, Si: 1% or less, Mn: 0 .1-1.5%, P: 0.03% or less, S
: 0.03% or less, Ni: 1% or less, Cr: 5 to 15%
, Mo: 0.02-3%, W: 4% or less, SolAl:
0.04% or less, N: 0.07% or less, and V: 0
．． For steel containing 0.01 to 0.4% and Nb: 0.01 to 0.3%, singly or in combination, and having Ac_1 of 820°C or higher, after normalizing at a temperature of Ac_3 or higher, 8
A method for producing high-strength, high-Cr ferritic steel, characterized in that high-temperature long-term creep strength is improved by tempering at a temperature of 10° C. or higher and Ac_1 or lower.
Priority Applications (7)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP22699485A JPS6289811A (en) | 1985-10-14 | 1985-10-14 | Manufacture of high-cr ferritic steel having high strength |
| US06/917,502 US4799972A (en) | 1985-10-14 | 1986-10-10 | Process for producing a high strength high-Cr ferritic heat-resistant steel |
| EP90125139A EP0427301B1 (en) | 1985-10-14 | 1986-10-13 | High-strength high-Cr ferritic heat-resistant steel |
| DE3650515T DE3650515T2 (en) | 1985-10-14 | 1986-10-13 | High-strength heat-resistant ferritic steel with a high chromium content |
| DE8686114164T DE3686121T2 (en) | 1985-10-14 | 1986-10-13 | HIGH-STRENGTH HEAT-RESISTANT FERRITIC STEEL WITH HIGH CHROME CONTENT AND METHOD FOR THE PRODUCTION THEREOF. |
| EP86114164A EP0219089B1 (en) | 1985-10-14 | 1986-10-13 | High-strength high-cr ferritic heat-resistant steel and process for producing the same |
| US07/232,227 US4957701A (en) | 1985-10-14 | 1988-08-15 | High-strength high-Cr ferritic heat-resistant steel |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP22699485A JPS6289811A (en) | 1985-10-14 | 1985-10-14 | Manufacture of high-cr ferritic steel having high strength |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS6289811A true JPS6289811A (en) | 1987-04-24 |
| JPH0459369B2 JPH0459369B2 (en) | 1992-09-22 |
Family
ID=16853845
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP22699485A Granted JPS6289811A (en) | 1985-10-14 | 1985-10-14 | Manufacture of high-cr ferritic steel having high strength |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS6289811A (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH04228547A (en) * | 1990-10-15 | 1992-08-18 | Nisshin Steel Co Ltd | Ferritic stainless steel excellent in intergranular corrosion resistance, tube making property, and strength at high temperature |
Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS58110661A (en) * | 1981-12-25 | 1983-07-01 | Hitachi Ltd | Heat resistant steel |
| JPS59116360A (en) * | 1982-12-24 | 1984-07-05 | Hitachi Ltd | Heat-resisting steel |
| JPS60155649A (en) * | 1984-01-25 | 1985-08-15 | Nippon Kokan Kk <Nkk> | Ferritic steel having superior strength at high temperature |
-
1985
- 1985-10-14 JP JP22699485A patent/JPS6289811A/en active Granted
Patent Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS58110661A (en) * | 1981-12-25 | 1983-07-01 | Hitachi Ltd | Heat resistant steel |
| JPS59116360A (en) * | 1982-12-24 | 1984-07-05 | Hitachi Ltd | Heat-resisting steel |
| JPS60155649A (en) * | 1984-01-25 | 1985-08-15 | Nippon Kokan Kk <Nkk> | Ferritic steel having superior strength at high temperature |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH04228547A (en) * | 1990-10-15 | 1992-08-18 | Nisshin Steel Co Ltd | Ferritic stainless steel excellent in intergranular corrosion resistance, tube making property, and strength at high temperature |
Also Published As
| Publication number | Publication date |
|---|---|
| JPH0459369B2 (en) | 1992-09-22 |
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