JPH066771B2 - Low alloy steel with excellent creep and hydrogen corrosion resistance - Google Patents
Low alloy steel with excellent creep and hydrogen corrosion resistanceInfo
- Publication number
- JPH066771B2 JPH066771B2 JP61160875A JP16087586A JPH066771B2 JP H066771 B2 JPH066771 B2 JP H066771B2 JP 61160875 A JP61160875 A JP 61160875A JP 16087586 A JP16087586 A JP 16087586A JP H066771 B2 JPH066771 B2 JP H066771B2
- Authority
- JP
- Japan
- Prior art keywords
- less
- hydrogen
- corrosion resistance
- alloy steel
- low alloy
- 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.)
- Expired - Fee Related
Links
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 title claims description 39
- 229910052739 hydrogen Inorganic materials 0.000 title claims description 39
- 239000001257 hydrogen Substances 0.000 title claims description 39
- 230000007797 corrosion Effects 0.000 title claims description 20
- 238000005260 corrosion Methods 0.000 title claims description 20
- 229910000851 Alloy steel Inorganic materials 0.000 title claims description 13
- 229910052719 titanium Inorganic materials 0.000 claims description 7
- 229910052796 boron Inorganic materials 0.000 claims description 6
- 229910052804 chromium Inorganic materials 0.000 claims description 6
- 229910052802 copper Inorganic materials 0.000 claims description 6
- 229910052750 molybdenum Inorganic materials 0.000 claims description 6
- 229910052758 niobium Inorganic materials 0.000 claims description 6
- 229910052720 vanadium Inorganic materials 0.000 claims description 6
- 239000012535 impurity Substances 0.000 claims description 5
- 229910052748 manganese Inorganic materials 0.000 claims description 5
- 229910052698 phosphorus Inorganic materials 0.000 claims description 5
- 229910052721 tungsten Inorganic materials 0.000 claims description 5
- 229910052726 zirconium Inorganic materials 0.000 claims description 5
- 230000000694 effects Effects 0.000 description 14
- 229910000831 Steel Inorganic materials 0.000 description 12
- 239000010959 steel Substances 0.000 description 12
- 230000003628 erosive effect Effects 0.000 description 11
- 229910052761 rare earth metal Inorganic materials 0.000 description 9
- 239000000463 material Substances 0.000 description 8
- 238000005336 cracking Methods 0.000 description 5
- 238000000137 annealing Methods 0.000 description 4
- 238000001816 cooling Methods 0.000 description 3
- 238000010791 quenching Methods 0.000 description 3
- 230000000171 quenching effect Effects 0.000 description 3
- 238000012360 testing method Methods 0.000 description 3
- 229910001566 austenite Inorganic materials 0.000 description 2
- 230000006866 deterioration Effects 0.000 description 2
- 230000007774 longterm Effects 0.000 description 2
- 229910052759 nickel Inorganic materials 0.000 description 2
- 238000005504 petroleum refining Methods 0.000 description 2
- 239000002994 raw material Substances 0.000 description 2
- 238000005496 tempering Methods 0.000 description 2
- 238000003466 welding Methods 0.000 description 2
- 239000000654 additive Substances 0.000 description 1
- 230000000996 additive effect Effects 0.000 description 1
- 230000002411 adverse Effects 0.000 description 1
- 229910045601 alloy Inorganic materials 0.000 description 1
- 239000000956 alloy Substances 0.000 description 1
- 229910052799 carbon Inorganic materials 0.000 description 1
- 230000000052 comparative effect Effects 0.000 description 1
- 239000010779 crude oil Substances 0.000 description 1
- 238000013461 design Methods 0.000 description 1
- 238000006477 desulfuration reaction Methods 0.000 description 1
- 230000023556 desulfurization Effects 0.000 description 1
- 238000011156 evaluation Methods 0.000 description 1
- 239000000295 fuel oil Substances 0.000 description 1
- 238000009499 grossing Methods 0.000 description 1
- 238000010438 heat treatment Methods 0.000 description 1
- 238000009863 impact test Methods 0.000 description 1
- 238000004519 manufacturing process Methods 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 238000000034 method Methods 0.000 description 1
- 239000000203 mixture Substances 0.000 description 1
- 229910052757 nitrogen Inorganic materials 0.000 description 1
- 238000007670 refining Methods 0.000 description 1
- 238000002407 reforming Methods 0.000 description 1
- 230000002040 relaxant effect Effects 0.000 description 1
- 238000011160 research Methods 0.000 description 1
- 229920006395 saturated elastomer Polymers 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
- 229910052717 sulfur Inorganic materials 0.000 description 1
Landscapes
- Heat Treatment Of Articles (AREA)
- Pressure Vessels And Lids Thereof (AREA)
Description
【発明の詳細な説明】 （産業上の利用分野） 石油精製工業、石油化学工業および一般化学工業におけ
る各種圧力容器や管類など、高温、高圧水素下で長期間
使用されるプラントの各部位材料に有利に適合するクリ
ープ特性および耐水素侵食特性の優れた低合金鋼に関す
る。DETAILED DESCRIPTION OF THE INVENTION (Industrial field of use) Materials for various parts of plants used for a long time under high temperature and high pressure hydrogen such as various pressure vessels and pipes in the petroleum refining industry, petrochemical industry and general chemical industry. The present invention relates to a low alloy steel excellent in creep property and hydrogen corrosion resistance property which is suitable for
石油精製工業における重油脱硫装置、原油改質装置等高
温高圧水素下で操業される圧力容器等には、従来耐水素
侵食特性に優れるCr−Mo鋼が使用されてきた。しかし生
産効率化のため操業条件はますます高温化、高水素圧化
の傾向にあり、容器の肉厚等の設計は高温短時間での強
度よりもむしろクリープ強さを基準に決定されるように
なってきた。したがって材料コスト削減、すなわち薄肉
化等のためにクリープ強さの向上がユーザーから強く求
められている。Cr-Mo steel, which is excellent in hydrogen erosion resistance, has been conventionally used for pressure vessels operated under high temperature and high pressure hydrogen such as heavy oil desulfurization equipment and crude oil reforming equipment in the petroleum refining industry. However, in order to improve production efficiency, operating conditions tend to become higher temperature and higher hydrogen pressure, and the design of container wall thickness, etc. is decided based on creep strength rather than strength at high temperature and short time. Has become. Therefore, in order to reduce the material cost, that is, to reduce the wall thickness, the improvement of creep strength is strongly demanded by users.
一方、操業条件はますます高温高水素圧化することか
ら、従来鋼に比べて格段に優れた耐水素侵食特性をそな
えていることも必要である。On the other hand, since the operating conditions are becoming increasingly high temperature and high hydrogen pressure, it is also necessary to have hydrogen erosion resistance properties that are far superior to those of conventional steel.
（従来の技術） 特開昭56-72156号公報には、Crを含有した低合金鋼にお
いてＶ，Ti，Ｂ等を適度に複合添加して、一定のクリー
プ強度の向上をはかることが開示されている。(Prior Art) Japanese Unexamined Patent Publication No. 56-72156 discloses that in a low alloy steel containing Cr, V, Ti, B and the like are appropriately added in combination to improve a certain creep strength. ing.
しかし、材料コスト削減のため、クリープ強さ向上への
要求は強く、上記公報にて規定された材料でも依然とし
て不十分であった。However, in order to reduce the material cost, there is a strong demand for improvement in creep strength, and the materials specified in the above publication are still insufficient.
（発明が解決しようとする問題点） 一般にCr−Mo鋼はオーステナイト領域での焼準または焼
入れ処理後、焼戻しまたは応力除去焼なまし処理(PWHT)
を施してじん性を確保している。焼戻しまたは応力除去
焼なまし処理の条件を緩和すればある程度の強度の向上
を確保することができるが、じん性は著しく劣化する。
じん性を確保しながら強度を著しく向上させるのは通常
成分のCr−Mo鋼では不可能で、合金元素を添加すること
により強度の向上をはかることが必要である。(Problems to be solved by the invention) Generally, in Cr-Mo steel, after normalizing or quenching treatment in the austenite region, tempering or stress relief annealing treatment (PWHT)
To ensure toughness. Relaxing the conditions of tempering or stress relieving annealing can secure some degree of improvement in strength, but the toughness is significantly deteriorated.
It is not possible to improve the strength remarkably while securing the toughness in the usual Cr-Mo steel, and it is necessary to improve the strength by adding an alloy element.
また単に熱処理条件を変更することにより、著しく耐水
素侵食性を向上させることは困難である。Further, it is difficult to remarkably improve the hydrogen corrosion resistance by simply changing the heat treatment conditions.
そこで適切な成分の含有によって、クリープ特性および
耐水素侵食特性の優れたCr−Mo鋼を提供することが、こ
の発明の目的である。Therefore, it is an object of the present invention to provide a Cr-Mo steel having excellent creep properties and hydrogen corrosion resistance properties by containing appropriate components.
（問題点を解決するための手段） 発明者らはCr含有低合金鋼のクリープ強さおよび水素侵
食特性に及ぼす添加成分の影響を巾広く検討した結果、
Cr鋼をベースとした鋼にＶ，Ｗを複合添加するとともに
低Ｎ、低Ｓにした場合、クリープ強さおよび耐水素侵食
特性ともに優れた材料が得られることを見い出し、この
発明に至った。(Means for Solving Problems) As a result of extensive studies on the effects of the additive components on the creep strength and hydrogen erosion characteristics of the Cr-containing low alloy steel,
It was found that a material excellent in creep strength and hydrogen corrosion resistance can be obtained when V and W are added together to a steel based on Cr steel and the N and S are made low, and the present invention has been completed.
すなわちこの発明は、Ｃ：0.05〜0.20wt％（以下単に％
と示す）、Si：0.50wt％以下、Mn：0.35〜1.5％、Cr：
2.0〜8.0％，Mo：0.1〜1.6％，Ｗ：0.50超〜2.5％，
Ｖ：0.05〜0.50％およびAl：0.06％以下を含み、かつ
Ｎ：0.0050％以下、Ｐ：0.010％以下およびＳ：0.004％
以下に抑制し、残部Ｆｅおよび不可避不純物よりなるク
リープ特性および耐水素侵食特性の優れた低合金鋼（第
１発明）、 第１発明にさらにNi：0.05〜1.0％、Ti：0.005〜0.08
％、Nb：0.005〜0.10％、Ｂ：0.0003〜0.006％、Cu：0.
05〜1.0％およびZr：0.005〜0.06％の１種または２種以
上を含有するクリープ特性および耐水素侵食特性の優れ
た低合金鋼（第２発明）、 第１発明にさらにＲＥＭ：0.001〜0.10％およびCa：0.0
01〜0.05％の１種又は２種を含有するクリープ特性およ
び耐水素侵食特性の優れた低合金鋼（第３発明）、 第１発明にさらにNi：0.05〜1.0％、Ti：0.005〜0.08
％、Nb：0.005〜0.10％、Ｂ：0.0003〜0.006％、Cu：0.
05〜1.0％、Zr：0.005〜0.06％の１種又は２種以上、お
よびＲＥＭ：0.001〜0.10％、Ca：0.001〜0.005％の１
種又は２種を含有するクリープ特性および耐水素侵食特
性の優れた低合金鋼（第４発明）、である。That is, the present invention is C: 0.05 to 0.20 wt% (hereinafter simply referred to as%
, Si: 0.50 wt% or less, Mn: 0.35 to 1.5%, Cr:
2.0 ~ 8.0%, Mo: 0.1 ~ 1.6%, W: Over 0.50 ~ 2.5%,
V: 0.05 to 0.50% and Al: 0.06% or less and N: 0.0050% or less, P: 0.010% or less and S: 0.004%
A low alloy steel (first invention) which is suppressed to the following and has excellent creep properties and hydrogen corrosion resistance properties consisting of the balance Fe and unavoidable impurities: Ni: 0.05 to 1.0%, Ti: 0.005 to 0.08
%, Nb: 0.005 to 0.10%, B: 0.0003 to 0.006%, Cu: 0.
Low alloy steel excellent in creep properties and hydrogen corrosion resistance (second invention) containing one or more of 05 to 1.0% and Zr: 0.005 to 0.06%, and REM: 0.001 to 0.10. % And Ca: 0.0
Low alloy steel containing 01 to 0.05% of 1 type or 2 type and excellent in creep characteristics and hydrogen corrosion resistance (third invention), Ni: 0.05 to 1.0%, Ti: 0.005 to 0.08 in addition to the first invention
%, Nb: 0.005 to 0.10%, B: 0.0003 to 0.006%, Cu: 0.
05-1.0%, Zr: 0.005-0.06%, one or more, and REM: 0.001-0.10%, Ca: 0.001-0.005%, 1
It is a low alloy steel (4th invention) excellent in creep property and hydrogen corrosion resistance property, which contains one or two kinds.
なお上記低合金鋼は、通常の手段にて製造される。The low alloy steel is manufactured by a usual method.
（作 用） 次に各成分の限定理由を述べる。(Working) Next, the reasons for limiting each component will be described.
Ｃ：0.05〜0.20％ Ｃは強度の確保及び脱酸のために0.05％以上の含有が必
要であるが0.20％をこえると溶接性が劣化するため、0.
05〜0.20％の範囲とする。C: 0.05 to 0.20% C needs to be contained in an amount of 0.05% or more to secure the strength and deoxidize, but if it exceeds 0.20%, the weldability deteriorates.
The range is from 05 to 0.20%.
Si：0.50％以下 Siが0.50％をこえて過剰に含有されると、焼戻しぜい化
感受性が増し、長期間の使用に際し材料がぜい化するお
それがあるので、0.50％以下に限定した。Si: 0.50% or less If Si is contained in excess of 0.50%, the susceptibility to temper embrittlement increases and the material may be embrittled during long-term use. Therefore, the content is limited to 0.50% or less.
Mn：0.35〜1.5％ 1.5％をこえる過度の含有は硬化による加工性の劣化を
まねき、また焼戻しぜい化感受性が増加するので、1.5
％を上限とする。一方、下限は焼入れ性を確保するため
に、0.35％とする。Mn: 0.35 to 1.5% Excessive content exceeding 1.5% leads to deterioration of workability due to hardening and increases susceptibility to temper embrittlement.
% Is the upper limit. On the other hand, the lower limit is 0.35% to secure hardenability.
Cr：2.0〜8.0％ 耐水素侵食特性の確保のためには少なくとも2.0％の含
有が必要である。しかし8.0％をこえる過剰の含有は原
料コストの上昇を招く一方、含有量に見合った改善効果
は得られないので、2.0〜8.0％の範囲とする。Cr: 2.0 to 8.0% At least 2.0% is necessary to secure hydrogen corrosion resistance. However, an excessive content of more than 8.0% causes an increase in raw material cost, but on the other hand, an improvement effect commensurate with the content cannot be obtained, so the content is made 2.0 to 8.0%.
Mo：0.1〜1.6％ Moは強度およびじん性の向上に効果があるが、含有量0.
1％未満ではその効果が不十分で、一方1.6％をこえて過
剰に含有させてもその効果は飽和し、不経済であるので
0.1〜1.6％の範囲とした。Mo: 0.1-1.6% Mo is effective in improving strength and toughness, but its content is 0.
If the content is less than 1%, the effect is insufficient. On the other hand, if the content exceeds 1.6% and the content is excessive, the effect is saturated and uneconomical.
The range was 0.1 to 1.6%.
Ｗ：0.50超〜2.5％ ＷはＶと組み合わせて0.50％をこえて含有させることに
よりクリープ破断強さ及びじん性の向上をはかることが
できる。しかし2.5％をこえて過剰に含有させた場合、
原料コストが上昇し、かつ含有量の割には向上効果が少
なくなるので、0.1〜2.5％の範囲とする。W: more than 0.50 to 2.5% By incorporating W in excess of 0.50% in combination with V, creep rupture strength and toughness can be improved. However, when it is contained in excess of 2.5%,
The raw material cost rises, and the improvement effect is small relative to the content, so the range is 0.1 to 2.5%.
Ｖ：0.50〜0.50％ ＶはＷと組み合わせて0.50％以上を含有させることによ
りクリープ強さ、耐水素侵食特性、および高温強度の向
上をはかることができる。しかし0.50％をこえる含有は
溶接性および溶接後の応力除去焼なまし時の割れに対す
る特性（耐ＳＲ割れ性）を劣化するので、0.50〜0.50％
の範囲とした。V: 0.50 to 0.50% By incorporating V in an amount of 0.50% or more in combination with W, creep strength, hydrogen corrosion resistance, and high temperature strength can be improved. However, if the content exceeds 0.50%, the weldability and the characteristics against cracking during stress relief annealing after welding (SR crack resistance) deteriorate, so 0.50 to 0.50%
And the range.
Ａｌ：0.06％以下 ＡｌはＮとＡｌＮを形成し、オーステナイト粒の微細化
に有効な成分であるが、0.06％をこえて含有させた場
合、耐水素侵食特性およびクリープ破断強さが低下し、
また熱間加工性の劣化が懸念されるため、0.06％以下と
する。なお下限は0.001％とすることが望ましい。Al: 0.06% or less Al forms an N and AlN and is an effective component for refining austenite grains, but when it is contained in excess of 0.06%, hydrogen corrosion resistance and creep rupture strength decrease,
In addition, since there is concern about deterioration of hot workability, it is set to 0.06% or less. The lower limit is preferably 0.001%.
Ｎ：0.0050％以下 低Ｎ化により耐水素侵食性が向上し、さらにクリープ強
さが向上すること、また0.0050％をこえて含有させた場
合、ブローホールの発生により製造性が阻害され、溶接
性も劣化するため、0.0050％以下とする。N: 0.0050% or less Improving hydrogen erosion resistance and creep strength by lowering N content. Also, if the content exceeds 0.0050%, manufacturability is hindered by the generation of blowholes and weldability. Also deteriorates, so 0.0050% or less.
Ｐ：0.010％以下 Ｐを0.010％をこえて含有させた場合焼戻しぜい化感受
性が増し、高温での長期間の使用にて材料が劣化するの
で、0.010％以下に限定する。P: 0.010% or less If P is contained in excess of 0.010%, susceptibility to temper embrittlement increases and the material deteriorates after long-term use at high temperature. Therefore, the content is limited to 0.010% or less.
Ｓ：0.004％以下 Ｓ量を低く抑えることにより水素侵食及び溶接後の応力
除去焼なまし時の割れ（ＳＲ割れ）に対する感受性を低
減させることは重要であり、Ｓ量を0.004％以下とする
ことで耐水素侵食特性、耐SR割れ性が向上するため、上
限を0.004％とする。S: 0.004% or less It is important to reduce the susceptibility to hydrogen erosion and cracks during stress relief annealing after welding (SR cracks) by suppressing the S content to a low level, and to set the S content to 0.004% or less. Therefore, hydrogen corrosion resistance and SR cracking resistance are improved, so the upper limit is made 0.004%.
以上が基本成分である。The above is the basic component.
また第２発明においては、上記基本成分のほか、以下の
各成分のうち１種又は２種以上を含有する。In the second invention, in addition to the above basic components, one or more of the following components are contained.
すなわちNi，Ti，Nb，Ｂ，CuおよびZrであり、これらの
成分はいずれも高温強度を向上する同一の作用効果を有
する。That is, they are Ni, Ti, Nb, B, Cu and Zr, and all of these components have the same action and effect of improving the high temperature strength.
Ni：0.05〜1.0％ Niは高温強度を高め、さらにじん性を向上させるが、0.
05％未満の含有ではその効果は不十分で、一方1.0％を
こえる含有は水素侵食および焼戻しぜい化に対する感受
性が増大するので、0.05〜1.0％の範囲とする。Ni: 0.05-1.0% Ni enhances high temperature strength and further improves toughness, but
If the content is less than 05%, the effect is insufficient, while if the content exceeds 1.0%, the susceptibility to hydrogen attack and temper embrittlement increases, so the content is made 0.05 to 1.0%.
Ti：0.005〜0.08％ Tiは高温強度を高め、さらにＮを固定してじん性の向上
をはかることができ、そのためには0.005％以上の含有
が必要であるが、0.08％をこえての含有はかえってじん
性を劣化し、また溶接性も悪化するため、0.005〜0.08
％の範囲とする。Ti: 0.005 to 0.08% Ti can enhance high temperature strength and further fix N to improve toughness. To this end, it is necessary to contain 0.005% or more, but more than 0.08% is included. On the contrary, the toughness deteriorates and the weldability also deteriorates.
The range is%.
Nb：0.005〜0.10％ 高温強度の向上を目的としてNbを含有させるが、その効
果を発揮させるには少なくとも0.005％の含有が必要で
あり、一方、0.10％をこえる含有は、溶接性が劣化する
ので、0.005〜0.10％の範囲とする。Nb: 0.005 to 0.10% Nb is contained for the purpose of improving high temperature strength, but at least 0.005% is necessary to exert its effect, while content exceeding 0.10% deteriorates weldability. Therefore, the range is 0.005 to 0.10%.
Ｂ：0.0003〜0.006％ 適量のＢの含有により高温強度を向上させることがで
き、その効果を発揮させるには少なくとも0.0003％の含
有が必要であるが、0.006％をこえる過度の含有は溶接
性が劣化するので、0.0003〜0.006％の範囲とする。B: 0.0003 to 0.006% By containing an appropriate amount of B, the high temperature strength can be improved, and at least 0.0003% is necessary to exert its effect, but an excessive content exceeding 0.006% results in poor weldability. Since it deteriorates, the range is 0.0003 to 0.006%.
Cu：0.05〜1.0％ Cuも高温強度を向上させる効果があり、この効果を発揮
させるには0.05以上の含有が必要であるが、1.0％をこ
えて過剰に含有させた場合、赤熱ぜい性を招くので0.05
〜1.0％の範囲とする。Cu: 0.05 to 1.0% Cu also has the effect of improving the high temperature strength, and it is necessary to contain 0.05 or more in order to exert this effect, but if it is contained in excess of 1.0%, the red hot brittleness Because it invites 0.05
The range is to 1.0%.
Zr：0.005〜0.06％ 適量のZrの含有により高温強度、さらにじん性を向上さ
せることができる。その効果を発揮させるには少なくと
も0.005％の含有が必要であるが、0.06％をこえて過剰
に含有させた場合、かえってじん性が劣化するので、0.
005〜0.06％の範囲とする。Zr: 0.005-0.06% By containing an appropriate amount of Zr, high temperature strength and toughness can be improved. It is necessary to contain at least 0.005% in order to exert its effect, but if it is contained in excess of 0.06%, the toughness rather deteriorates.
The range is 005 to 0.06%.
さらに第３発明においては上記基本成分のほか、次に示
すＲＥＭおよびCaの１種または２種以上を含有し、また
第４発明において第２発明の成分のほか、次に示すＲＥ
ＭおよびCaの１種又は２種以上を含有する。なおこの発
明におけるＲＥＭは、Ｙを含む希土類元素から選ばれる
１種又は２種以上を意味し、ＲＥＭおよびCaはＳを固定
して耐水素侵食特性および耐ＳＲ割れ性を向上させる同
一の作用効果を有する。Further, in the third invention, in addition to the above basic components, one or more of REM and Ca shown below are contained, and in addition to the components of the second invention in the fourth invention, RE shown below is also contained.
It contains one or more of M and Ca. In addition, REM in the present invention means one or more selected from rare earth elements including Y, and REM and Ca have the same function and effect to fix S and improve hydrogen corrosion resistance and SR cracking resistance. Have.
ＲＥＭ：0.001〜0.10％ ＲＥＭを含有させる目的はＳを固定して耐水素侵食特性
および耐ＳＲ割れ性を向上させることにあり、そのため
には0.001％以上の含有が必要である。しかし0.10％を
こえて含有させた場合、じん性が劣化するので、0.001
〜0.10％の範囲とする。REM: 0.001 to 0.10% The purpose of containing REM is to fix S and improve hydrogen corrosion resistance and SR cracking resistance, and for that purpose, 0.001% or more is necessary. However, if the content exceeds 0.10%, the toughness deteriorates, so 0.001
The range is to 0.10%.
Ca：0.001〜0.05％ CaもＲＥＭと同様に0.001％以上の含有によりＳを固定
して耐水素侵食特性および耐ＳＲ割れ性を向上させる。
しかし0.05％以上の含有の場合鋼中の介在物が多くな
り、じん性等に悪影響を及ぼすので、0.001〜0.05％の
範囲とする。Ca: 0.001 to 0.05% Similar to REM, Ca also contains 0.001% or more to fix S and improve hydrogen corrosion resistance and SR cracking resistance.
However, when the content is 0.05% or more, the inclusions in the steel increase, which adversely affects toughness, etc., so the range is 0.001 to 0.05%.
（実施例） 表１に示す組成の鋼を、それぞれ真空溶解炉にて溶製
し、次いで16mm厚に熱間圧延後1050℃で２時間保持して
焼入れ、690℃で24.5時間の応力除去焼なまし処理(PWH
T)を行って試料とした。焼入れ（800℃→400℃）の平均
冷却速度は15℃/minにコントロールした。この冷却速度
は300mm厚の鋼板を水冷した場合の中心部の冷却速度に
相当する。(Examples) Steels having the compositions shown in Table 1 were melted in a vacuum melting furnace, then hot-rolled to a thickness of 16 mm, held at 1050 ° C for 2 hours for quenching, and stress-relieved at 690 ° C for 24.5 hours. Smoothing (PWH
T) was performed to make a sample. The average cooling rate of quenching (800 ℃ → 400 ℃) was controlled at 15 ℃ / min. This cooling rate corresponds to the cooling rate of the central portion when a 300 mm thick steel plate is water-cooled.
ＰＷＨＴ後クリープ試験および水素侵食試験を行った。Post PWHT creep and hydrogen erosion tests were performed.
耐水素侵食特性の評価は、試料を600℃、500kgf/cm2の
高温、高圧水素に最高2000時間暴露後、シャルピー衝撃
試験を０℃にて行い、そのときの吸収エネルギーvE0と
暴露時間との関係を調べ、vE0の低下の始まる時間を水
素侵食の潜伏期とし、この潜伏期を耐水素侵食特性の指
標とした。The evaluation of hydrogen erosion resistance was conducted by exposing the sample to 600 ° C, high temperature of 500kgf / cm 2 and high pressure hydrogen for up to 2000 hours, and then performing a Charpy impact test at 0 ° C. The absorbed energy vE 0 and the exposure time Was examined, and the time when the decrease of vE 0 started was defined as the latency of hydrogen erosion, and this latency was used as an index of the hydrogen erosion resistance property.
表１に、クリープ試験結果および水素侵食の潜伏期の測
定結果を示す。また第１図に、表１に示すクリープ破断
までの時間および試験温度を、ラーソンミラーパラメー
タにて整理した上で負荷応力との関係として示す。Table 1 shows the results of the creep test and the results of measuring the latent period of hydrogen attack. Further, in FIG. 1, the time until creep rupture and the test temperature shown in Table 1 are shown as a relationship with the load stress after being arranged by the Larson Miller parameters.
表１および第１図から、この発明に適合する鋼は比較例
に比べ、クリープ破断強さが格段に高く、また耐水素侵
食特性も優れていることがわかる。It can be seen from Table 1 and FIG. 1 that the steels conforming to the present invention have markedly higher creep rupture strength and superior hydrogen erosion resistance characteristics as compared with the comparative examples.
（発明の効果） この発明に従う鋼は高いクリープ破断強さおよび優れた
耐水素侵食特性をそなえ、したがって高温、高圧水素下
にて長期間操業される圧力容器および管類用材料に有利
に適合する。 (Effect of the Invention) The steel according to the present invention has high creep rupture strength and excellent resistance to hydrogen erosion, and is therefore advantageously suited to materials for pressure vessels and pipes that are operated for a long time under high temperature and high pressure hydrogen. .
第１図は、クリープ破断応力とラーソンミラーパラメー
タとの関係を示すグラフである。FIG. 1 is a graph showing the relationship between creep rupture stress and Larson Miller parameters.
───────────────────────────────────────────────────── フロントページの続き (72)発明者 上田 修三 千葉県千葉市川崎町１番地 川崎製鉄株式 会社技術研究本部内 (72)発明者 藤田 利夫 東京都文京区向丘１丁目14の４ (56)参考文献 特開 昭61−52354（ＪＰ，Ａ) ─────────────────────────────────────────────────── ─── Continuation of the front page (72) Inventor Shuzo Ueda, 1 Kawasaki-cho, Chiba-shi, Chiba Kawasaki Steel Co., Ltd. Technical Research Headquarters (72) Inventor Toshio Fujita 1-14-14, Mukooka, Bunkyo-ku, Tokyo (56) References JP-A-61-52354 (JP, A)
Claims (4)
び耐水素侵食特性の優れた低合金鋼。1. C: 0.05 to 0.20 wt%, Si: 0.50 wt% or less, Mn: 0.35 to 1.5 wt%, Cr: 2.0 to 8.0 wt%, Mo: 0.1 to 1.6 wt%, W: more than 0.50 to 2.5 wt%, V: 0.05 to 0.50 wt% and Al: 0.06 wt% or less, and N: 0.0050 wt% or less, P: 0.010 wt% or less and S: 0.004 wt% or less, balance Fe and unavoidable A low alloy steel with excellent creep properties and hydrogen corrosion resistance consisting of impurities.
0.005〜0.10wt％，Ｂ：0.0003〜0.006wt％，Cu：0.05〜
1.0wt％およびZr：0.005〜0.06wt％の１種又は２種以上
を含有し、残部Feおよび不可避不純物よりなるクリープ
特性および耐水素侵食特性の優れた低合金鋼。2. C: 0.05 to 0.20 wt%, Si: 0.50 wt% or less, Mn: 0.35 to 1.5 wt%, Cr: 2.0 to 8.0 wt%, Mo: 0.1 to 1.6 wt%, W: over 0.50 to 2.5 wt%, V: 0.50 to 0.50 wt% and Al: 0.06 wt% or less, and N: 0.0050 wt% or less, P: 0.010 wt% or less and S: 0.004 wt% or less, and Ni: 0.05 to 1.0wt%, Ti: 0.005-0.08wt%, Nb:
0.005-0.10wt%, B: 0.0003-0.006wt%, Cu: 0.05-
A low alloy steel containing 1.0 wt% and Zr: 0.005 to 0.06 wt% of one kind or two or more kinds, and consisting of the balance Fe and unavoidable impurities and having excellent creep characteristics and hydrogen corrosion resistance.
％の１種又は２種を含有し、残部Feおよび不可避不純物
よりなるクリープ特性および耐水素侵食特性の優れた低
合金鋼。3. C: 0.05 to 0.20 wt%, Si: 0.50 wt% or less, Mn: 0.35 to 1.5 wt%, Cr: 2.0 to 8.0 wt%, Mo: 0.1 to 1.6 wt%, W: more than 0.50 to 2.5 wt%, V: 0.05 to 0.50 wt% and Al: 0.06 wt% or less, and N: 0.0050 wt% or less, P: 0.010 wt% or less, and S: 0.004 wt% or less, and REM: 0.001 ~ 0.10wt% and Ca: 0.001-0.05wt
% Low alloy steel containing 1% or 2% and having the balance of Fe and unavoidable impurities and having excellent creep characteristics and hydrogen corrosion resistance.
0.005〜0.10wt％， Ｂ：0.0003〜0.006wt％，Cu：0.05〜1.0wt％，Zr：0.00
5〜0.06wt％の１種または２種以上、およびＲＥＭ：0.0
01〜0.10wt％，Ca：0.001〜0.005wt％の１種又は２種を
含有し、残部Fe及び不可避不純物よりなるクリープ特性
および耐水素侵食特性の優れた低合金鋼。4. C: 0.05-0.20 wt%, Si: 0.50 wt% or less, Mn: 0.35-1.5 wt% or less, Cr: 2.0-8.0 wt%, Mo: 0.1-1.6 wt%, W: over 0.50- 2.5 wt%, V: 0.05 to 0.50 wt% and Al: 0.06 wt% or less, and N: 0.0050 wt% or less, P: 0.010 wt% or less and S: 0.004 wt% or less, and Ni: 0.05 ~ 1.0wt%, Ti: 0.005-0.08wt%, Nb:
0.005-0.10wt%, B: 0.0003-0.006wt%, Cu: 0.05-1.0wt%, Zr: 0.00
5 to 0.06 wt% of 1 or 2 or more, and REM: 0.0
A low alloy steel containing 01 to 0.10 wt% and Ca: 0.001 to 0.005 wt%, one or two, with the balance being Fe and unavoidable impurities and having excellent creep properties and hydrogen corrosion resistance.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP61160875A JPH066771B2 (en) | 1986-07-10 | 1986-07-10 | Low alloy steel with excellent creep and hydrogen corrosion resistance |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP61160875A JPH066771B2 (en) | 1986-07-10 | 1986-07-10 | Low alloy steel with excellent creep and hydrogen corrosion resistance |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS6318038A JPS6318038A (en) | 1988-01-25 |
| JPH066771B2 true JPH066771B2 (en) | 1994-01-26 |
Family
ID=15724258
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP61160875A Expired - Fee Related JPH066771B2 (en) | 1986-07-10 | 1986-07-10 | Low alloy steel with excellent creep and hydrogen corrosion resistance |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH066771B2 (en) |
Families Citing this family (12)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH0250941A (en) * | 1988-08-12 | 1990-02-20 | Nippon Steel Corp | Stainless steel with excellent carbon dioxide corrosion resistance and stress corrosion cracking resistance |
| JPH062927B2 (en) * | 1989-02-20 | 1994-01-12 | 住友金属工業株式会社 | High strength low alloy steel with excellent corrosion resistance and oxidation resistance |
| JPH062926B2 (en) * | 1989-02-20 | 1994-01-12 | 住友金属工業株式会社 | Heat resistant steel with high temperature creep strength |
| JP2967886B2 (en) * | 1991-02-22 | 1999-10-25 | 住友金属工業 株式会社 | Low alloy heat resistant steel with excellent creep strength and toughness |
| JP3334217B2 (en) * | 1992-03-12 | 2002-10-15 | 住友金属工業株式会社 | Low Cr ferritic heat resistant steel with excellent toughness and creep strength |
| JP3096959B2 (en) * | 1996-02-10 | 2000-10-10 | 住友金属工業株式会社 | Low Mn and low Cr ferrite heat resistant steel with excellent high temperature strength |
| JP3745567B2 (en) | 1998-12-14 | 2006-02-15 | 新日本製鐵株式会社 | Boiler steel excellent in ERW weldability and ERW boiler steel pipe using the same |
| JP3518515B2 (en) | 2000-03-30 | 2004-04-12 | 住友金属工業株式会社 | Low / medium Cr heat resistant steel |
| GB2364715B (en) * | 2000-07-13 | 2004-06-30 | Toshiba Kk | Heat resistant steel casting and method of manufacturing the same |
| CN100393903C (en) * | 2005-08-26 | 2008-06-11 | 首钢总公司 | High-toughness low-alloy constructional steel and producing method thereof |
| EP2474433B1 (en) | 2009-09-04 | 2020-04-29 | Toyota Jidosha Kabushiki Kaisha | Electrically-driven vehicle |
| JP7502623B2 (en) | 2019-08-13 | 2024-06-19 | 日本製鉄株式会社 | Low alloy heat-resistant steel and steel pipes |
Family Cites Families (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS6152354A (en) * | 1984-08-20 | 1986-03-15 | Kobe Steel Ltd | Low-alloy steel for pressure vessel |
-
1986
- 1986-07-10 JP JP61160875A patent/JPH066771B2/en not_active Expired - Fee Related
Also Published As
| Publication number | Publication date |
|---|---|
| JPS6318038A (en) | 1988-01-25 |
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