JPH04198458A - Heat resisting steel excellent in carburizing resistance and creep rupture strength - Google Patents
Heat resisting steel excellent in carburizing resistance and creep rupture strengthInfo
- Publication number
- JPH04198458A JPH04198458A JP33627890A JP33627890A JPH04198458A JP H04198458 A JPH04198458 A JP H04198458A JP 33627890 A JP33627890 A JP 33627890A JP 33627890 A JP33627890 A JP 33627890A JP H04198458 A JPH04198458 A JP H04198458A
- Authority
- JP
- Japan
- Prior art keywords
- creep rupture
- rupture strength
- heat resisting
- resisting steel
- resistance
- 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
- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 21
- 239000010959 steel Substances 0.000 title claims abstract description 21
- 238000005255 carburizing Methods 0.000 title abstract description 7
- 229910052758 niobium Inorganic materials 0.000 claims abstract description 9
- 229910052799 carbon Inorganic materials 0.000 claims abstract description 7
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 7
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 5
- 229910052759 nickel Inorganic materials 0.000 claims abstract description 5
- 229910052719 titanium Inorganic materials 0.000 claims abstract description 3
- 239000000463 material Substances 0.000 abstract description 14
- 238000006243 chemical reaction Methods 0.000 abstract description 5
- 229930195733 hydrocarbon Natural products 0.000 abstract description 5
- 150000002430 hydrocarbons Chemical class 0.000 abstract description 5
- 239000004215 Carbon black (E152) Substances 0.000 abstract description 3
- 238000000034 method Methods 0.000 abstract description 3
- 239000000203 mixture Substances 0.000 abstract description 3
- 230000000694 effects Effects 0.000 description 15
- 229910045601 alloy Inorganic materials 0.000 description 8
- 239000000956 alloy Substances 0.000 description 8
- 230000007423 decrease Effects 0.000 description 8
- 238000005266 casting Methods 0.000 description 4
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 3
- 230000006866 deterioration Effects 0.000 description 3
- 230000008018 melting Effects 0.000 description 3
- 238000002844 melting Methods 0.000 description 3
- 230000003647 oxidation Effects 0.000 description 3
- 238000007254 oxidation reaction Methods 0.000 description 3
- 238000005979 thermal decomposition reaction Methods 0.000 description 3
- 238000006057 reforming reaction Methods 0.000 description 2
- 239000007787 solid Substances 0.000 description 2
- 238000007711 solidification Methods 0.000 description 2
- 230000008023 solidification Effects 0.000 description 2
- 238000003466 welding Methods 0.000 description 2
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 1
- OTMSDBZUPAUEDD-UHFFFAOYSA-N Ethane Chemical compound CC OTMSDBZUPAUEDD-UHFFFAOYSA-N 0.000 description 1
- 229910001566 austenite Inorganic materials 0.000 description 1
- 238000009750 centrifugal casting Methods 0.000 description 1
- 239000003795 chemical substances by application Substances 0.000 description 1
- 230000000052 comparative effect Effects 0.000 description 1
- 230000008094 contradictory effect Effects 0.000 description 1
- 229910052802 copper Inorganic materials 0.000 description 1
- 239000010949 copper Substances 0.000 description 1
- 230000003009 desulfurizing effect Effects 0.000 description 1
- 230000001771 impaired effect Effects 0.000 description 1
- 239000012535 impurity Substances 0.000 description 1
- 239000004615 ingredient Substances 0.000 description 1
- 229910052742 iron Inorganic materials 0.000 description 1
- 238000003754 machining Methods 0.000 description 1
- 150000001247 metal acetylides Chemical class 0.000 description 1
- 229910052750 molybdenum Inorganic materials 0.000 description 1
- 239000000843 powder Substances 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 229920006395 saturated elastomer Polymers 0.000 description 1
- 230000002195 synergetic effect Effects 0.000 description 1
- 229910052721 tungsten Inorganic materials 0.000 description 1
Landscapes
- Heat Treatment Of Steel (AREA)
- Solid-Phase Diffusion Into Metallic Material Surfaces (AREA)
Abstract
Description
【発明の詳細な説明】
[産業上の利用分野]
本発明は、石油化学工業におけるナフサ、エタン等の炭
化水素の熱分解・改質反応に使用される反応管等の材料
として好適な耐熱鋼に関する。[Detailed Description of the Invention] [Field of Industrial Application] The present invention relates to a heat-resistant steel suitable as a material for reaction tubes, etc. used in the thermal decomposition and reforming reactions of hydrocarbons such as naphtha and ethane in the petrochemical industry. Regarding.
[従来技術及びその問題点]
石油化学工業における炭化水素の熱分解・改質反応では
、炭化水素の熱分解過程にて、カーボンが反応管の壁面
に付着し、そのカーボンが管の内部に拡散していくため
、いわゆる浸炭現象が生じて反応管の材質が著しく劣化
する問題がある。[Prior art and its problems] In the thermal decomposition and reforming reactions of hydrocarbons in the petrochemical industry, carbon adheres to the wall of the reaction tube during the hydrocarbon thermal decomposition process, and the carbon diffuses into the inside of the tube. As a result, a so-called carburization phenomenon occurs, resulting in significant deterioration of the material of the reaction tube.
この用途に使用される材料として、従来から、ASTM
に規定されたH P系材料(25Cr−35Ni)や、
さらにNb、W、Mo等を添加した改良HP系材料等が
広く使用されている。The materials used for this purpose have traditionally been ASTM
HP material (25Cr-35Ni) specified in
Furthermore, improved HP materials to which Nb, W, Mo, etc. are added are widely used.
ところで、最近では、操業温度の高温化が進んでおり、
上記材料の場合、1100°C以上の温度で使用される
と、十分の耐浸炭性を発揮できないばかりか、クリープ
破断強度の著しい低下を招くという問題がある。このた
め、1100℃以」二の温度域での使用に耐え得るすぐ
れた耐浸炭性と高いクリープ破断強度を備えた材料が要
請されている。By the way, recently, operating temperatures have been increasing,
In the case of the above-mentioned materials, when used at a temperature of 1100° C. or higher, there is a problem that not only is sufficient carburization resistance not exhibited, but the creep rupture strength is significantly reduced. Therefore, there is a need for a material that has excellent carburization resistance and high creep rupture strength that can withstand use in a temperature range of 1100° C. or higher.
本発明はかかる要請を満たした新規な材料を提供するも
のである。The present invention provides a novel material that satisfies such requirements.
[技術的手段及び作用]
本発明の耐熱鋼は、重量%にて、C:0.3〜15%、
Si・2%を超えて3%以下、M1]:2%以下、Cr
:20−30%、Ni:25−40%、A1:0.2〜
20%、Nb:’0.2〜20%および残部実質的にF
eからなる成分組成を有している。[Technical means and effects] The heat-resistant steel of the present invention contains C: 0.3 to 15% in weight%;
Si: more than 2% and less than 3%, M1]: less than 2%, Cr
:20-30%, Ni:25-40%, A1:0.2~
20%, Nb:'0.2-20% and the remainder substantially F
It has a component composition consisting of e.
本発明の耐熱鋼は、必要に応じて、さらにTi:0.0
1〜03%を含有することもできる。The heat-resistant steel of the present invention may further include Ti: 0.0 if necessary.
It can also contain 1 to 03%.
本発明の耐熱鋼は、1100℃以上の温度域の使用にお
いて、すぐれた耐浸炭性と高いクリープ破断強度を具備
している。The heat-resistant steel of the present invention has excellent carburization resistance and high creep rupture strength when used in a temperature range of 1100° C. or higher.
[成分限定理由] 本発明の耐熱鋼の成分限定理由は次の通りである。[Reason for limited ingredients] The reasons for limiting the components of the heat-resistant steel of the present invention are as follows.
C:0.3〜15%
CBの増加に伴って溶融温度が低下するため、鋳造性が
向上する。しかし、あまりに含有量が多くなると、材料
の劣化か進み、鋳造割れや溶接割れを発生する。このた
め、C含有量の上限は15%とする。C: 0.3 to 15% Since the melting temperature decreases as CB increases, castability improves. However, if the content is too high, the material deteriorates and cracks in casting and welding occur. Therefore, the upper limit of the C content is set to 15%.
他方、C含有量か03%より少ないと高温での使用中に
シグマ相が析出し、延性の著しい低下を招く。このため
、下限は03%に規定する。On the other hand, if the C content is less than 0.3%, a sigma phase will precipitate during use at high temperatures, resulting in a significant decrease in ductility. Therefore, the lower limit is defined as 0.3%.
Si ・2%を超えて3%以下 Siは耐浸炭性を向上させる重要な元素である。Si ・More than 2% and less than 3% Si is an important element that improves carburization resistance.
また、後記するようにA1も耐浸炭性を向上させる重要
な元素である。本発明者は、1100°Cを超える温度
での耐浸炭性を確保するため、特にAf!とSiとの関
係について鋭意研究した結果、Siの含有量が2%以下
のときは、A1含有による耐浸炭性向」二効果はあまり
期待できないことを見出した。このため、Slは少なく
とも2%を超えて含有させる必要がある。しかし、Si
の含有量を多くすると、材料の劣化が進み、クリープ破
断強度が低下して溶接性が損なわれるので、その」1限
は3%に規定する。Furthermore, as described later, A1 is also an important element that improves carburization resistance. In order to ensure carburization resistance at temperatures exceeding 1100°C, the inventors have specifically identified Af! As a result of intensive research on the relationship between steel and Si, it was found that when the Si content is 2% or less, no significant effect on carburization resistance due to A1 content can be expected. Therefore, it is necessary to contain at least 2% of Sl. However, Si
If the content of Cr is increased, the deterioration of the material progresses, the creep rupture strength decreases, and weldability is impaired, so the limit is set at 3%.
Mn 2%以下
Mnは脱酸、脱硫元素として添加される。しかし、あま
りに多く含有すると、高温クリープ破断強度や耐浸炭性
の低下を招来する。このため、」1限は2%に規定する
。Mn 2% or less Mn is added as a deoxidizing and desulfurizing element. However, if it is contained in an excessively large amount, the high-temperature creep rupture strength and carburization resistance will be reduced. Therefore, the first limit is set at 2%.
Cr:20−30%
Crは高温強度、耐酸化性、耐浸炭性等の改善に有効な
元素である。1100°C以上の高温域においてこれら
の特性を確保するためには、少なくとも20%含有させ
る必要がある。この効果は含有量の増加に伴って増大す
るが、あまりに多く含有すると鋳造、凝固過程で割れか
生じやすくなり、高温使用に伴う炭化物の過剰析出によ
って、延性の低下を招く。このため、」−眼は30%に
規定する。Cr: 20-30% Cr is an element effective in improving high temperature strength, oxidation resistance, carburization resistance, etc. In order to ensure these properties in a high temperature range of 1100°C or higher, it is necessary to contain at least 20%. This effect increases as the content increases, but if the content is too large, cracks are likely to occur during casting and solidification processes, and excessive precipitation of carbides due to use at high temperatures leads to a decrease in ductility. Therefore, "-eye" is defined as 30%.
N1・25〜40%
N1はCr、Mn等の元素と共に安定なオーステナイト
基地を形成し、高温強度及び耐酸化性を高めるとともに
、耐浸炭性の向上に寄与する。特に1100°C以」二
の高温域における良好な耐浸炭性を確保するには、25
%以」二の添加を必要とする。N1・25-40% N1 forms a stable austenite base together with elements such as Cr and Mn, and contributes to improving high temperature strength and oxidation resistance as well as carburization resistance. In particular, in order to ensure good carburization resistance in the high temperature range of 1100°C or higher, 25
% or more is required.
しかし、40%を超えて含有しても含有量に対応する効
果は得られず、経済的でない。このため、40%を」1
限とする。However, even if the content exceeds 40%, the effect corresponding to the content cannot be obtained and it is not economical. For this reason, 40%”1
limited.
Al:0.2〜20%
Aeは、高温における耐酸化性の改善に効果があるだけ
でなく、前述したように、Si含有量が2%を超えると
き、Siとの相乗効果によって耐浸炭性の向上に飛躍的
に寄与する。1100℃以」二の高温使用条件下での耐
浸炭性改善効果を十分発揮させるためには、少なくとも
02%含有させる必要がある。耐浸炭性改善効果は、添
加惜の増加に伴って大きくなるが、20%を超えて添加
してもその効果はほぼ飽和する。また、A1の含有量の
増加とともに、鋳造凝固時や溶接時に割れか発生しやす
くなり、高温使用時に延性の劣化を招く。このため、2
%を上限にする。Al: 0.2-20% Ae is not only effective in improving oxidation resistance at high temperatures, but as mentioned above, when the Si content exceeds 2%, it improves carburization resistance due to its synergistic effect with Si. dramatically contribute to the improvement of In order to fully exhibit the effect of improving carburization resistance under high-temperature usage conditions of 1100° C. or higher, it is necessary to contain at least 0.2%. The effect of improving carburization resistance increases as the addition amount increases, but even if it is added in excess of 20%, the effect is almost saturated. Furthermore, as the content of A1 increases, cracks are more likely to occur during casting solidification and welding, leading to deterioration of ductility during high-temperature use. For this reason, 2
% is the upper limit.
Nb : 0.2〜20% Nbはクリープ破断強度を高める効果を有する。Nb: 0.2-20% Nb has the effect of increasing creep rupture strength.
Si含有量が多く、かつAI!を添加した本発明の耐熱
鋼にあっては、高温強度、特にクリープ破断強度を低下
させる不都合があるため、すぐれた耐浸炭性を確保し、
かつ大きいクリープ破断強度を維持するためには不可欠
の元素である。この効果を得るために、少なくとも0.
2%以上含有する必要がある。但し、あまりに多く含有
すると、逆にクリープ破断強度の低下を招くため、20
%を」1限とする。なお、Nbは通常これと同効の元素
であるTaを随伴するものであり、この場合にはTaと
の合計量が0.2〜20%であればよい。High Si content and AI! In the heat-resistant steel of the present invention, which has been added with
Moreover, it is an essential element in order to maintain high creep rupture strength. To obtain this effect, at least 0.
It is necessary to contain 2% or more. However, if it is contained too much, it will cause a decrease in creep rupture strength.
% is set to 1 limit. Note that Nb usually accompanies Ta, which is an element with the same effect as Nb, and in this case, the total amount with Ta should be 0.2 to 20%.
T i + 0.01−0.3%
TiはNbと同様にクリープ破断強度を高める効果を有
するため、さらに大きいクリープ破断強度を必要とする
場合に添加される。Tiによる所望の効果を得るために
は、少なくとも0.01%以」二含有させる必要がある
。しかし、あまり多く含有すると、逆にクリープ破断強
度の低下を招くと共に、鋳造割れを発生する。このため
、−L限は0.3%に規定する。Ti + 0.01-0.3% Since Ti has the effect of increasing creep rupture strength like Nb, it is added when even higher creep rupture strength is required. In order to obtain the desired effect of Ti, it is necessary to contain it in an amount of at least 0.01%. However, if the content is too large, the creep rupture strength will decrease and casting cracks will occur. Therefore, the -L limit is defined as 0.3%.
本発明の耐熱鋼は、前述した合金成分を含み、残部実質
的にFeからなる。なお、鋼の溶製時に不可避的に含有
するPXSその他の不純物であっても、この種の銅相に
通常許容される範囲であれば存在しても構わない。The heat-resistant steel of the present invention contains the above-mentioned alloy components, with the remainder substantially consisting of Fe. It should be noted that PXS and other impurities that are unavoidably contained during the melting of steel may be present as long as they are within the range normally allowed for this type of copper phase.
次に実施例を挙げて本発明の耐熱鋼における耐浸炭性及
びクリープ破断強度の向上効果を明らかにする。Next, Examples will be given to clarify the effect of improving carburization resistance and creep rupture strength in the heat-resistant steel of the present invention.
[実施例]
高周波溶解炉にて各種成分の合金を溶製し、遠心鋳造に
て管体(外径130mmX内径90mmX長さ500ミ
リ)を製造した。この遠心力鋳造管から機械加工によっ
て供試片(直径12mmX長さ60mm)を採取した。[Example] An alloy of various components was melted in a high frequency melting furnace, and a tube body (outer diameter 130 mm x inner diameter 90 mm x length 500 mm) was manufactured by centrifugal casting. A specimen (diameter 12 mm x length 60 mm) was collected from this centrifugally cast tube by machining.
各供試片の合金成分を第1表に示す。The alloy composition of each specimen is shown in Table 1.
ます、これらの供試片について、固体浸炭試験を行なっ
た。浸炭試験は、固体浸炭剤(テグサKG30、BaC
O3含有)を用いて行ない、温度1150℃、500時
間保持後の浸炭量を測定した。浸炭後、供試片の外表面
より4mm深さに達するまで旋盤加工により0.5mm
ピッチにてダライ粉を採取し、各ピッチのC(カーボン
)分析を行ない、各ピッチ毎のC増加量の合計値を第2
表に示した。First, solid carburization tests were conducted on these specimens. The carburizing test was conducted using a solid carburizing agent (Tegusa KG30, BaC
The amount of carburization was measured after holding the temperature at 1150° C. for 500 hours. After carburizing, the specimen was lathed to a depth of 0.5 mm from the outer surface until it reached a depth of 4 mm.
Collect powder at each pitch, conduct C (carbon) analysis on each pitch, and calculate the total amount of C increase for each pitch as a second
Shown in the table.
更に、各供試片について、1093℃X 1 、1kg
/mm2の条件下でクリープ破断試験を行ない、各供試
片の破断時間を第2表に示した。Furthermore, for each specimen, 1093℃X 1, 1kg
A creep rupture test was conducted under the condition of /mm2, and the rupture time of each specimen is shown in Table 2.
(以下余白)
第2表
供試片 クリープ′断試馴 −一一浸炭試験
一−NOクリープ破断時間(Hrs) 表面から4
mmまでの1093℃X 1 伽/mm2C増加量のA
ト(%)1 1112
2.842 1108
2.763 960
2.714 ’ 1215
2.635 1630
2.716 1510
2.657 1010
2.518 1153
2.409 976
2.3810 10
15 2.3811
1361 2.3012
1532 2.2813
1005 16.7614
901 10.24
15 773 10.
7116 553 4
.4117 310
2.2118 530
3.2619 690
8.70比較祠の供試片No、13〜19の結果に
ついて考察する。供試片No、13とN015はSiが
2%に満たない合金であり、N013についてはA1を
含有せず、No、15はAeを含有している。No、1
4とNo、16−19は、Si含有量が2%を超えてい
る合金である。(Left below) Table 2 Specimen Creep rupture test - 11 Carburizing test 1 - NO creep rupture time (Hrs) 4 from the surface
A of 1093℃ x 1 C/mm2C increase amount up to mm
(%) 1 1112
2.842 1108
2.763 960
2.714' 1215
2.635 1630
2.716 1510
2.657 1010
2.518 1153
2.409 976
2.3810 10
15 2.3811
1361 2.3012
1532 2.2813
1005 16.7614
901 10.24
15 773 10.
7116 553 4
.. 4117 310
2.2118 530
3.2619 690
8.70 The results of comparative shrine test pieces Nos. 13 to 19 will be discussed. Specimens No. 13 and No. 15 are alloys containing less than 2% Si, with No. 13 containing no A1 and No. 15 containing Ae. No.1
No. 4, No. 16-19 are alloys in which the Si content exceeds 2%.
その中で、No、14はAIを含まず、No、19はA
Iの含有量が02%に満たない合金、No16〜18は
02%以上のA1を含む合金である。Among them, No. 14 does not include AI, No. 19 includes A
Alloys with an I content of less than 0.2%, Nos. 16 to 18 are alloys containing A1 of 0.2% or more.
この結果から明らかなように、供試片No、16〜18
は、No、13〜15に比べてCの増加量は著しく減少
している。即ち、耐浸炭性にすぐれている。なお、供試
片No、19は、A1含有量が少ないため、耐浸炭性に
関し、顕著な向上効果は認められなかった。As is clear from this result, specimen Nos. 16 to 18
The amount of increase in C was significantly reduced compared to Nos. 13 to 15. That is, it has excellent carburization resistance. In addition, since sample No. 19 had a low A1 content, no significant improvement effect was observed in terms of carburization resistance.
一方、Si含有量が2%を超える合金にApを含有させ
れば、クリープ破断強度が低下する傾向がある。特に供
試片No、17のように、高Si1高いA+2材料の場
合、クリープ破断強度の低下は著しい。On the other hand, if Ap is included in an alloy having a Si content of more than 2%, the creep rupture strength tends to decrease. In particular, in the case of a high Si1 high A+2 material such as specimen No. 17, the creep rupture strength decreases significantly.
これに対し、供試片No、1〜12については、Si含
有量が2%を超える材料に適量のAp2を含有させ、更
に適量のNb、又はNb及びTiを含有させたから、す
ぐれた耐浸炭性を維持しつつ、がつ高いクリープ破断強
度を具備している。このように、耐浸炭性とクリープ破
断強度は、相反する特性であるに拘わらす、本発明の耐
熱鋼は、両者ともすぐれた特性を有している。On the other hand, specimens Nos. 1 to 12 had excellent carburization resistance because they contained an appropriate amount of Ap2 and further contained an appropriate amount of Nb or Nb and Ti in a material with a Si content of more than 2%. It has extremely high creep rupture strength while maintaining its properties. Thus, although carburization resistance and creep rupture strength are contradictory properties, the heat-resistant steel of the present invention has excellent properties in both.
[発明の効果]
本発明の耐熱鋼は、1100°Cを超える高温域におけ
る使用において、すぐれた耐浸炭性と、高いクリープ破
断強度を具備している。従って、本発明の耐熱鋼は、石
油化学工業における炭化水素の反応管等の材料として好
適である。[Effects of the Invention] The heat-resistant steel of the present invention has excellent carburization resistance and high creep rupture strength when used in a high temperature range exceeding 1100°C. Therefore, the heat-resistant steel of the present invention is suitable as a material for hydrocarbon reaction tubes and the like in the petrochemical industry.
Claims (2)
を超えて3%以下、Mn:2%以下、Cr:20〜30
%、Ni:25〜40%、Al:0.2〜20%、Nb
:0.2〜20%及び残部実質的にFeからなり、耐浸
炭性及びクリープ破断強度にすぐれる耐熱鋼。(1) In weight%, C: 0.3-1.5%, Si: 2%
exceeding 3%, Mn: 2% or less, Cr: 20-30
%, Ni: 25-40%, Al: 0.2-20%, Nb
:0.2 to 20%, and the balance substantially consists of Fe, and is a heat-resistant steel with excellent carburization resistance and creep rupture strength.
を超えて3%以下、Mn:2%以下、Cr:20〜30
%、Ni:25〜40%、Al:0.2〜2.0%、N
b:0.2〜2.0%、Ti:0.01〜0.3%及び
残部実質的にFeからなり、耐浸炭性及びクリープ破断
強度にすぐれる耐熱鋼。(2) In weight%, C: 0.3-1.5%, Si: 2%
exceeding 3%, Mn: 2% or less, Cr: 20-30
%, Ni: 25-40%, Al: 0.2-2.0%, N
A heat-resistant steel consisting of b: 0.2 to 2.0%, Ti: 0.01 to 0.3%, and the balance substantially Fe, and has excellent carburization resistance and creep rupture strength.
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP33627890A JPH07103449B2 (en) | 1990-11-28 | 1990-11-28 | Heat-resistant steel with excellent carburization resistance and creep rupture strength |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP33627890A JPH07103449B2 (en) | 1990-11-28 | 1990-11-28 | Heat-resistant steel with excellent carburization resistance and creep rupture strength |
Publications (2)
Publication Number | Publication Date |
---|---|
JPH04198458A true JPH04198458A (en) | 1992-07-17 |
JPH07103449B2 JPH07103449B2 (en) | 1995-11-08 |
Family
ID=18297459
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
JP33627890A Expired - Lifetime JPH07103449B2 (en) | 1990-11-28 | 1990-11-28 | Heat-resistant steel with excellent carburization resistance and creep rupture strength |
Country Status (1)
Country | Link |
---|---|
JP (1) | JPH07103449B2 (en) |
-
1990
- 1990-11-28 JP JP33627890A patent/JPH07103449B2/en not_active Expired - Lifetime
Also Published As
Publication number | Publication date |
---|---|
JPH07103449B2 (en) | 1995-11-08 |
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