JPS6052560A - High cr-mo steel - Google Patents
High cr-mo steelInfo
- Publication number
- JPS6052560A JPS6052560A JP16014883A JP16014883A JPS6052560A JP S6052560 A JPS6052560 A JP S6052560A JP 16014883 A JP16014883 A JP 16014883A JP 16014883 A JP16014883 A JP 16014883A JP S6052560 A JPS6052560 A JP S6052560A
- Authority
- JP
- Japan
- Prior art keywords
- steel
- toughness
- long
- strength
- less
- 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.)
- Pending
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- Heat Treatment Of Steel (AREA)
Abstract
Description
【発明の詳細な説明】 本発明は原子力用部材として好適で、溶接性。[Detailed description of the invention] The present invention is suitable as a nuclear power member and has good weldability.
高温強度及び靭性にす（゛れ高温での長時間使用による
脆化の少ない高Ｃｒ−Ｍｏ鋼に関するものである。This relates to a high Cr-Mo steel that has good high-temperature strength and toughness (and is less prone to embrittlement due to long-term use at high temperatures).
従来、火力用熱交換器の管及び管板には２１／４％Ｏｒ
−］％Ｍｏ鋼（例えばＡＣＭＥＳＡ１８２Ｆ２２ ）な
どが多用されているが、原子力用には、Ｎａ及び水との
共存性の優れた高Ｃｒ−Ｍｏ鋼の使用が必須である。ま
た、原子力用材料は極度の安全性を要求される。Conventionally, 21/4% Or
-]%Mo steel (for example, ACMESA182F22) is often used, but for nuclear power applications, it is essential to use a high Cr-Mo steel that has excellent coexistence with Na and water. In addition, materials for nuclear power require extreme safety.
原子力用高Ｃｒ−Ｍｏ鋼としては、その使用温度が８５
０〜５５０℃と比較的低いが、高Ｃｒ−Ｍｏ鋼はこの温
度域で長時間使用（加熱）されると、著しい脆化を起こ
す。これはもっと使用温度の高い火力用材料では問題視
されなかった問題である。そこで、原子カプラントの安
全性・信頼性を向上させるため ２１／４％０ｒ−１％
Ｍｏ鋼よりも高温強度が高（、じん性が良好であり、耐
長時間使用（加熱）脆化にも優れ、溶接性の良好な高Ｃ
ｒ−Ｍｏ鋼の開発が強（要望されている。As a high Cr-Mo steel for nuclear power use, its operating temperature is 85
Although the temperature is relatively low at 0 to 550°C, high Cr-Mo steel undergoes significant embrittlement when used (heated) in this temperature range for a long time. This is a problem that was not considered a problem with materials for thermal power, which are used at higher temperatures. Therefore, in order to improve the safety and reliability of nuclear couplants, 21/4%0r-1%
High-temperature strength (higher temperature strength than Mo steel), good toughness, resistance to long-term use (heating) embrittlement, and good weldability.
There is strong demand for the development of r-Mo steel.
本発明は、上記の要求を満たすために１本発明者等が鋭
意研究した結果完成したもので、従来の高Ｃｒ−Ｍｏ鋼
よりも高温強度、じん性に優れ。The present invention was completed as a result of intensive research by the inventors in order to meet the above requirements, and has superior high temperature strength and toughness than conventional high Cr-Mo steel.
長時間使用（加熱）による脆化を低減し、溶接性を改良
した高Ｃｒ−Ｍｏ鋼を提供するにある。It is an object of the present invention to provide a high Cr-Mo steel with reduced embrittlement due to long-term use (heating) and improved weldability.
即ち１本発明の要旨とするところは２重量比で、 ０
： ０．０１〜０．０８％、 Ｓｉ ： ０．０１〜０
．１２％、 Ｍｎ＝ ００１〜２ ％ｌ Ｐ ： ≦０
．０１ ％、 Ｓ ： ≦００１ ％。That is, 1. The gist of the present invention is 2. The weight ratio is 0.
: 0.01~0.08%, Si: 0.01~0
．． 12%, Mn=001~2%l P: ≦0
．． 01%, S: ≦001%.
Ｃ「ニア〜ｌＯ％、 Ｍｎ ： ０．５〜２．５％、
Ｎｌ） ： ０．１％以下。C "Near to lO%, Mn: 0.5 to 2.5%,
Nl): 0.1% or less.
Ｎｉ：１％以下、 Ａｌ ： ０．０１〜００３％、
Ｎ ： ０．０７％以下を含有し、残部はＦｅと不可避
不純物とよりなる高温強度、じん性に優れ、長時間使用
（加熱）による脆化の少ない、溶接性の優れた高Ｏｒ−
Ｍｏ鋼である。Ni: 1% or less, Al: 0.01-003%,
N: Contains 0.07% or less, with the remainder consisting of Fe and unavoidable impurities. High Or-
It is Mo steel.
次に本発明の成分を限定した理由を下記に詳細説明する
。Next, the reason for limiting the components of the present invention will be explained in detail below.
Ｃは必要となる引張強さを向上させるために有効な成分
でＱ、０１２以上必要であるが、００８％を超えると長
時間使用（加熱）により２粒界炭化物の析出が著しく増
加して脆化を促進する。C is an effective component to improve the required tensile strength, and Q is required to be at least 0.012%, but if it exceeds 0.08%, precipitation of two-grain boundary carbides will significantly increase due to long-term use (heating), resulting in brittleness. promote the development of
８１は溶鋼の脱酸剤として必要であるが、成分組成が０
１２％を超えるとじん性及び耐長時間使用（加熱）脆化
の低下をもたらし、０．０１％未満では強度低下をもた
らすため、その範囲として００１〜０１２％とした。81 is necessary as a deoxidizing agent for molten steel, but its composition is 0.
If it exceeds 12%, the toughness and long-term use (heating) embrittlement will decrease, and if it is less than 0.01%, the strength will decrease, so the range is set to 001 to 012%.
Ｍｎは脱酸剤、加工性改善のため添加されるものである
が、過剰添加すると側熱特性を劣化させる故、００１〜
２０％とした。Mn is added as a deoxidizing agent and to improve processability, but excessive addition deteriorates side heat properties, so
It was set at 20%.
Ｐは不可避不純物であるが、その含有量が００１％を超
えると長時間使用（加熱）にょる脆化を促進させるので
、上限値を０．０１％とした。P is an unavoidable impurity, but if its content exceeds 0.01%, it will promote embrittlement due to long-term use (heating), so the upper limit was set at 0.01%.
Ｓは不可避不純物であるが、その含有量が０．０１％を
超えると、じん性を劣化させる鋼中のＡ系非金属介在物
（硫化物）が著しく増加するため、その上限値を００１
％とした。S is an unavoidable impurity, but if its content exceeds 0.01%, A-based nonmetallic inclusions (sulfides) in steel that deteriorate toughness will increase significantly.
%.
Ｃｒは、Ｎａ及び水との共存性に優れた効果を示すが、
７％未満ではＮａ及び水との共存性が劣り。Cr shows excellent coexistence with Na and water, but
If it is less than 7%, coexistence with Na and water is poor.
１０％を超えるとじん性を劣化させる故、７〜１０％と
した。If it exceeds 10%, the toughness deteriorates, so it was set at 7 to 10%.
Ｍｏは、主として固溶強化元素として高温強度向−Ｆに
有効であるが、過剰に添加すると加工性が悪くなり１合
金の組織を不安定にして脆化相を析出させ、少なすぎる
と高温強度向上に寄与しないので、０５〜２５％の範囲
に限定する必要がある。Mo is mainly effective as a solid solution strengthening element for high-temperature strength. However, when added in excess, the workability deteriorates and the structure of the alloy becomes unstable, leading to the precipitation of a brittle phase. When too little is added, the high-temperature strength decreases. Since it does not contribute to improvement, it is necessary to limit it to a range of 05 to 25%.
Ｎｂは１組織を微細にし、じん性及び耐長時間使用（加
熱）脆化を向」ユさせる効果を示すが。Nb has the effect of making the structure finer and improving toughness and resistance to long-term use (heating) embrittlement.
０１％を超えて添加すると溶接性を損なうため。Adding more than 0.01% impairs weldability.
０．１％以下とした。尚、００２％以上とすると効果が
顕著となり好ましい。It was set to 0.1% or less. Incidentally, it is preferable to set the content to 0.002% or more because the effect becomes remarkable.
Ｎｉは、じん性を向」ニさせる効果を示すが、１％を超
えて添加すると著しく硬化させるので。Ni exhibits the effect of improving toughness, but when added in excess of 1%, it causes significant hardening.
１％以下とした。尚、 ０．０１％以上とするとその効
果が顕著となり好ましい。It was set to 1% or less. Incidentally, when the content is 0.01% or more, the effect becomes remarkable and it is preferable.
Ｎは、Ｃと同様に強力なオーステナイト形成元素であり
、ｒ相を安定化させ、じん性を向上させる効果を示すが
、００７％を超えて添加すると、インゴット製造時に鋼
塊中に著しい気泡を生じ、鋼質を損ねるので、０．０７
％以下とした。N, like C, is a strong austenite-forming element and has the effect of stabilizing the r-phase and improving toughness, but if added in excess of 0.07%, significant air bubbles may be created in the steel ingot during ingot production. 0.07 because it causes damage to the steel quality.
% or less.
尚、００１％以」−含有させるとその効果が顕著となり
好ましい。Incidentally, it is preferable to include 0.001% or more because the effect becomes remarkable.
Ａ１は、脱酸剤として極めて有効な元素であり。A1 is an extremely effective element as a deoxidizing agent.
鋼の清浄度に大きな効果を有する。原子力用鋼材は鋼の
内部欠陥、清浄度に対する要求が厳格であり、これを満
足させるためには、００１％未満では効果がなく、Ｏ，
Ｏａ％を超えると高温強度を損ねるので０．０１〜０．
０３％とした。It has a great effect on the cleanliness of steel. Steel materials for nuclear power use have strict requirements regarding internal defects and cleanliness of the steel, and in order to satisfy these requirements, it is ineffective if it is less than 0.001%, and O,
If it exceeds 0.01 to 0.0%, the high temperature strength will be impaired.
03%.
次に本発明を実施例によって詳細説明する。Next, the present invention will be explained in detail by way of examples.
本発明及び本発明の成分組成に属さない高Ｏｒ−Ｍｏ鋼
を比較例として強度、じん性、溶接性について試験した
。The present invention and high Or-Mo steels that do not belong to the composition of the present invention were tested for strength, toughness, and weldability as comparative examples.
これらの成分組成を第１表に示し２強度試験結果を第２
表、じん性（熱処理まま、長時間加熱後）の試験結果を
第８表、溶接最高硬さを第４表に示す。These component compositions are shown in Table 1 and the results of the 2nd strength test are shown in Table 2.
Table 8 shows the test results for toughness (as heat treated and after long-term heating), and Table 4 shows the maximum welding hardness.
第１表に示すこれらの鋼は、溶解・鍛造後に熱処理とし
て９５０℃にて１時間保持後に空冷し。After melting and forging, these steels shown in Table 1 were heat treated at 950° C. for 1 hour and then cooled in air.
引き続いて焼もどしを７５０℃で１時間で行なった。Tempering was subsequently carried out at 750° C. for 1 hour.
第２表に示すとおり、引張強度、クリープラブチャー強
度は発明鋼と比較鋼を大きな相違は認められないが、若
干発明鋼の強度が高めになる。As shown in Table 2, there is no significant difference in tensile strength and creep rupture strength between the invented steel and the comparative steel, but the strength of the invented steel is slightly higher.
一方、第３表に示すように、０℃吸収エネルギーは本発
明鋼と比較鋼では相違がみられ、熱処理ままでは総じて
吸収エネルギーが大きい。On the other hand, as shown in Table 3, there is a difference in absorbed energy at 0° C. between the invention steel and the comparative steel, and the absorbed energy is generally large when heat treated.
さらに温度５５０℃で＋０００１＋の長時間加熱後には
発明鋼と比較鋼の吸収エネルギーの相違が歴然となり２
発明鋼ではせいぜい４〜５ｋｇｆ−ｍの低下にとどまり
、しかもその吸収エネルギー値は実用的にも十分良好な
値である。一方、比較鋼の場合には吸収エネルギーは５
〜Ｉ Ｏｋｇ「−ｍはど長時間加熱により低下し、かつ
低下後の吸収エネルギーはもっと低い場合には２．９
ｋｇｆ−ｍとなり、原子力用に適用する場合不十分と考
えられる。発明鋼に示されるような高じん性は原子力用
に適用する場合、定期点検後の水圧試験の際の不安定破
壊、地震などの衝撃的変形に対する安全性の点から極め
て望ましい性質である。Furthermore, after long-term heating at +0001+ at a temperature of 550°C, the difference in absorbed energy between the invented steel and the comparison steel became obvious2.
In the invention steel, the decrease is only 4 to 5 kgf-m at most, and the absorbed energy value is a sufficiently good value for practical use. On the other hand, in the case of comparative steel, the absorbed energy is 5
~I Okg'-m decreases with long-term heating, and if the absorbed energy after the decrease is lower, it is 2.9
kgf-m, which is considered insufficient when applied to nuclear power. The high toughness shown in the invented steel is an extremely desirable property when applied to nuclear power applications from the viewpoint of safety against unstable fracture during hydraulic pressure tests after periodic inspections and impact deformation due to earthquakes and the like.
第４表には溶接最高硬さを示すが、溶接性難易の一つの
基準であるｎｖ≦４００を発明鋼は満足（７）
するのに対して、比較鋼Ｇ、Ｈ，ＪはＨＶ ４００ Ｊ
超えている。鋼Ｆ’、Ｉ、 ＫｉｄＨｖ≦４００以下で
はあるが、第３表に示すごとく長時間加燃後の衝撃特性
が問題である。Table 4 shows the maximum welding hardness, and the invention steel satisfies nv≦400, which is one criterion for weldability (7), whereas comparative steels G, H, and J have HV 400 J.
Over. Although steel F', I, KidHv≦400 or less, as shown in Table 3, the impact properties after long-term combustion are a problem.
第１表 供試鋼の化学成分
（８）
第２表 供試鋼の機械的性質
第８表 長時間加熱援吻性
第４表 溶接最高硬さ
以上説明したとおり１本発明の合金は、高温強度、靭性
に優れ、長時間使用しても脆化が起こりにくい上に溶接
性にもすく゛れるので、原子炉用部材として最適である
ほか、各種高温用機器部材として好適である。Table 1 Chemical composition of the test steel (8) Table 2 Mechanical properties of the test steel Table 8 Long-term heating support property Table 4 Maximum welding hardness As explained above, the alloy of the present invention is It has excellent strength and toughness, is resistant to embrittlement even after long-term use, and has excellent weldability, making it ideal for use as parts for nuclear reactors as well as for various high-temperature equipment parts.
Claims (1)
０．０１〜Ｏ１２゜Ｍｎ ： ０．０１−２ 、 Ｐ
：≦Ｏ，Ｏ＋、Ｓ：≦０．０１ 、 Ｏｒ ニア 〜
１０． Ｍｏ ： ０．５〜２．５． Ｎｂ ： ０．
１以下、Ｎｉ：１以下。 Ａｌ ： ０．０１〜０．０Ｂ 、 Ｎ ： ０．０７
以下、残部Ｆｅ及び不可避不純物からなることを特徴と
し、高温強度。 靭性に優れ、長時間使用による脆化の少ない。 溶接性に優れた高Ｃｒ−Ｍｏ鋼。[Claims] In weight %, a: O, O1-0.08, 8+:
0.01~O12°Mn: 0.01-2, P
:≦O, O+, S:≦0.01, Or near ~
10. Mo: 0.5-2.5. Nb: 0.
1 or less, Ni: 1 or less. Al: 0.01-0.0B, N: 0.07
Below, the balance is characterized by consisting of Fe and unavoidable impurities, and high temperature strength. Excellent toughness and less embrittlement due to long-term use. High Cr-Mo steel with excellent weldability.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP16014883A JPS6052560A (en) | 1983-08-31 | 1983-08-31 | High cr-mo steel |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP16014883A JPS6052560A (en) | 1983-08-31 | 1983-08-31 | High cr-mo steel |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPS6052560A true JPS6052560A (en) | 1985-03-25 |
Family
ID=15708903
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP16014883A Pending JPS6052560A (en) | 1983-08-31 | 1983-08-31 | High cr-mo steel |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS6052560A (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS62103344A (en) * | 1985-07-25 | 1987-05-13 | Nippon Kokan Kk <Nkk> | Nine percent chromium heat-resisting steel reduced in sensitivity to low-and high-temperature cracking, excellent in toughness, and having high creep strength at welded joint |
-
1983
- 1983-08-31 JP JP16014883A patent/JPS6052560A/en active Pending
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS62103344A (en) * | 1985-07-25 | 1987-05-13 | Nippon Kokan Kk <Nkk> | Nine percent chromium heat-resisting steel reduced in sensitivity to low-and high-temperature cracking, excellent in toughness, and having high creep strength at welded joint |
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