JP3524708B2 - Carbon steel with excellent high-temperature strength - Google Patents
Carbon steel with excellent high-temperature strengthInfo
- Publication number
- JP3524708B2 JP3524708B2 JP00293897A JP293897A JP3524708B2 JP 3524708 B2 JP3524708 B2 JP 3524708B2 JP 00293897 A JP00293897 A JP 00293897A JP 293897 A JP293897 A JP 293897A JP 3524708 B2 JP3524708 B2 JP 3524708B2
- Authority
- JP
- Japan
- Prior art keywords
- carbon steel
- temperature strength
- strength
- steel
- 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.)
- Expired - Fee Related
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- Heat Treatment Of Steel (AREA)
Description
【０００１】[0001]
【発明の属する技術分野】本発明は発電用ボイラ、ター
ビン及び化学プラント等の分野で、高温耐圧部材として
使用するのに好適な高温強度に優れた炭素鋼に関する。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a carbon steel excellent in high temperature strength suitable for use as a high temperature pressure resistant member in the fields of power generation boilers, turbines, chemical plants and the like.
【０００２】[0002]
【従来の技術】高温配管用炭素鋼鋼管（ＪＩＳ Ｇ ３
４５６）、配管用合金鋼鋼管（ＪＩＳＧ ３４５８）、
配管用ステンレス鋼（ＪＩＳ Ｇ ３４５９）、ボイラ
・熱交換器用炭素鋼鋼管（ＪＩＳ Ｇ ３４６１）、ボ
イラ・熱交換器用合金鋼鋼管（ＪＩＳ Ｇ ３４６２）
及びボイラ・熱交換器用ステンレス鋼管（ＪＩＳ Ｇ３
４６３）が、また近年では耐酸化性に有効な元素である
Ｃｒを９〜１２％含有する高強度フェライト系耐熱鋼等
が発電プラント用鋼管として広く利用されている。2. Description of the Related Art Carbon steel pipes for high temperature piping (JIS G 3
456), alloy steel pipe for piping (JISG 3458),
Stainless steel for piping (JIS G 3459), carbon steel pipe for boiler / heat exchanger (JIS G 3461), alloy steel pipe for boiler / heat exchanger (JIS G 3462)
And stainless steel tubes for boilers and heat exchangers (JIS G3
463), and in recent years, high-strength ferritic heat-resistant steel containing 9 to 12% of Cr, which is an element effective in oxidation resistance, has been widely used as a steel pipe for power plants.
【０００３】[0003]
【発明が解決しようとする課題】発電用ボイラ・熱交換
器などの高温環境下で使用される材料に最も要求される
特性はクリープ強度と耐酸化性である。現在、発電用プ
ラントにおいては、上記のとおり幅広い成分範囲の材料
が使用されているが、このうち、ステンレス鋼や９〜１
２％Ｃｒ鋼は高温強度に優れ、かつＣｒを含有している
ため耐酸化性に優れているが、合金元素を多量に含有し
ていることから非常に高価である。したがって、これら
鋼は耐酸化性に有効な元素であるＣｒやＮｉ等を含有し
ない炭素鋼よりも高い環境温度で使用されている。Creep strength and oxidation resistance are the most required characteristics for materials used in high temperature environments such as boilers and heat exchangers for power generation. Currently, in power generation plants, materials with a wide range of components as described above are used. Among them, stainless steel and 9 to 1 are used.
2% Cr steel is excellent in high-temperature strength and is excellent in oxidation resistance because it contains Cr, but it is very expensive because it contains a large amount of alloying elements. Therefore, these steels are used at a higher environmental temperature than carbon steels that do not contain elements such as Cr and Ni that are effective for oxidation resistance.
【０００４】一方、炭素鋼はステンレス鋼や合金鋼に比
べて安価であるが、耐酸化性が劣るために５００℃未満
の温度で使用されている。また、これらの温度域に使用
される耐圧部材では、炭素鋼のクリープ強度が低いため
に、設計応力上高価な合金鋼を使用するか管厚を厚くし
なければならず、材料コストが高くなる。On the other hand, although carbon steel is less expensive than stainless steel and alloy steel, it is used at a temperature of less than 500 ° C. because of its poor oxidation resistance. Further, in the pressure resistant member used in these temperature ranges, since the creep strength of carbon steel is low, it is necessary to use expensive alloy steel or increase the pipe thickness due to the design stress, which increases the material cost. .
【０００５】本発明は上記技術水準に鑑み、低コストか
つ高温強度に優れた炭素鋼を提供しようとするものであ
る。In view of the above-mentioned state of the art, the present invention is to provide a carbon steel which is low in cost and excellent in high temperature strength.
【０００６】[0006]
【課題を解決するための手段】本発明はＮｂとＶの適量
添加によって、母地に析出物を微細分散させて高温強度
を向上させてなる炭素鋼であって、下記構成（１）〜
（５）を有するものである。The present invention is a carbon steel in which precipitates are finely dispersed in a matrix to improve high-temperature strength by adding an appropriate amount of Nb and V, and the following constitution (1) to
It has (5).
【０００７】すなわち、本発明は（１）Ｃ：０．０１〜
０．１ｗｔ％、Ｓｉ：０．１５〜０．５ｗｔ％、Ｍｎ：
０．４〜２ｗｔ％、Ｎｂ：０．０１〜０．１ｗｔ％、
Ｖ：０．０１〜０．３ｗｔ％を含有し、残部がＦｅ及び
不可避的不純物からなり、母地中に微細な析出物が分散
していることを特徴とする高温強度に優れた炭素鋼、
（２）上記（１）の炭素鋼において、Ｂを５０ｐｐｍ以
下含有してなることを特徴とする高温強度に優れた炭素
鋼、（３）上記（１）の炭素鋼において、Ｍｏ及びＷの
１種以上を含有し、その含有量がＭｏ＋１／２Ｗで０．
５〜２ｗｔ％の範囲であることを特徴とする高温強度に
優れた炭素鋼、（４）上記（１）の炭素鋼において、Ｔ
ａ，Ｈｆ，Ｚｒ，Ｏｓのうち１種以上の合計含有量とし
て０．１〜４ｗｔ％含有してなることを特徴とする高温
強度に優れた炭素鋼、（５）上記（１）の炭素鋼におい
て、上記（２）〜（４）に示した補助添加材を２項目以
上複合添加させてなることを特徴とする高温強度に優れ
た炭素鋼である。That is, the present invention is (1) C: 0.01-
0.1 wt%, Si: 0.15-0.5 wt%, Mn:
0.4-2 wt%, Nb: 0.01-0.1 wt%,
V: containing 0.01～0.3Wt%, balance Ri Do Fe and inevitable impurities, fine precipitates in the mother ground dispersion
Excellent carbon steel in high temperature strength to be to have characterized Rukoto,
(2) The carbon steel of (1) above, which contains B in an amount of 50 ppm or less, is excellent in high-temperature strength, (3) In the carbon steel of (1) above, 1 of Mo and W is included. It contains more than one kind, and when the content is Mo + 1 / 2W, 0.
Carbon steel excellent in high temperature strength, characterized in that it is in the range of 5 to 2 wt%, (4) in the carbon steel of (1) above, T
Carbon steel excellent in high-temperature strength, characterized by containing 0.1 to 4 wt% as a total content of at least one of a, Hf, Zr and Os, (5) Carbon steel according to (1) above. smell
Then , the carbon steel excellent in high-temperature strength is characterized in that the auxiliary additives shown in the above (2) to (4) are added in combination of two or more items.
【０００８】[0008]
【発明の実施の形態】本発明鋼の各合金成分の効果とそ
の組成範囲の限定理由について以下に述べる。BEST MODE FOR CARRYING OUT THE INVENTION The effect of each alloy component of the steel of the present invention and the reason for limiting the composition range will be described below.
【０００９】１）Ｃ：ＣはＮｂ，Ｖと結合して微細な炭
化物を形成し、高温強度を向上させる。しかし、０．０
１ｗｔ％未満では炭化物の生成量が少なく高温強度が向
上しない。また、０．１ｗｔ％を超えて添加するとセメ
ンタイト（Ｆｅ3 Ｃ）が析出し、靱性を阻害すると同時
に溶接性を悪くする。したがって、その添加範囲を０．
０１〜０．１ｗｔ％（望ましくは０．０２〜０．０６ｗ
ｔ％）とした。1) C: C combines with Nb and V to form fine carbides and improve high temperature strength. But 0.0
If it is less than 1 wt%, the amount of carbide produced is small and the high temperature strength is not improved. Further, if added in excess of 0.1 wt%, cementite (Fe 3 C) precipitates, impairs toughness and, at the same time, deteriorates weldability. Therefore, the addition range is set to 0.
01-0.1 wt% (preferably 0.02-0.06w
t%).
【００１０】２）Ｓｉ：Ｓｉは製鋼時の脱酸及び強度の
維持を考えて０．１５〜０．５ｗｔ％とした。2) Si: Si is set to 0.15 to 0.5 wt% in consideration of deoxidation during steelmaking and maintenance of strength.
【００１１】３）Ｍｎ：Ｍｎは脱酸のためのみでなく、
強度保持上も必要な成分であり、０．４ｗｔ％未満では
十分な効果が得られない。一方、２ｗｔ％を超すと靱性
が悪くなるので、０．４〜２ｗｔ％（望ましくは１．２
〜２ｗｔ％）の範囲とした。3) Mn: Mn is not only for deoxidation,
It is also a component necessary for maintaining strength, and if it is less than 0.4 wt%, a sufficient effect cannot be obtained. On the other hand, if it exceeds 2 wt%, the toughness deteriorates, so 0.4 to 2 wt% (preferably 1.2)
.About.2 wt%).
【００１２】４）Ｎｂ，Ｖ：Ｎｂ及びＶは本発明の骨子
となる元素であり、Ｃと結合して微細な炭化物を形成す
る。この炭化物は４５０℃以上のクリープ温度域におい
ても非常に安定であり、転位の運動を阻害することによ
って高温強度を向上させる。しかし、これらの元素は
０．０１ｗｔ％未満では全く効果がなく、また、Ｎｂは
０．１ｗｔ％、Ｖは０．３ｗｔ％を超えて添加しても効
果が飽和するのでその添加範囲をＮｂは０．０１〜０．
１ｗｔ％（望ましくは０．０３〜０．０８ｗｔ％）、Ｖ
は０．１〜０．３ｗｔ％（望ましくは０．１〜０．２５
ｗｔ％）とした。4) Nb, V: Nb and V are elements that are the essence of the present invention, and combine with C to form fine carbides. This carbide is very stable even in the creep temperature range of 450 ° C. or higher, and improves the high temperature strength by inhibiting the movement of dislocations. However, if these elements are less than 0.01 wt%, there is no effect, and if Nb is added in excess of 0.1 wt% and V is added in excess of 0.3 wt%, the effect is saturated. 0.01-0.
1 wt% (desirably 0.03 to 0.08 wt%), V
Is 0.1 to 0.3 wt% (desirably 0.1 to 0.25
wt%).
【００１３】５）Ｂ：Ｂは侵入型元素として母相中に固
溶し、高温強度を向上させる。しかし、多すぎるとホウ
化物を形成し靱性及び延性を低下させるのでその上限を
５０ｐｐｍ（望ましくは２０〜４０ｐｐｍ）とした。5) B: B dissolves in the matrix as an interstitial element and improves the high temperature strength. However, if the amount is too large, boride is formed to reduce toughness and ductility, so the upper limit was made 50 ppm (desirably 20 to 40 ppm).
【００１４】６）Ｍｏ，Ｗ：Ｍｏ及びＷは母相中に固溶
して転位の上昇運動速度を低下させ、４５０℃以上の高
温でも強度の向上に有効に寄与する。しかし、これらの
元素はＭｏ＋１／２Ｗが０．５ｗｔ％未満では効果がな
く、また２ｗｔ％を超えて添加すると高温においてＦｅ
との金属間化合物であるＬａｖｅｓ相を形成するため
に、その効果が飽和する。したがって、添加範囲をＭｏ
＋１／２Ｗで０．５〜２ｗｔ％（望ましくは０．５〜
１．５ｗｔ％）とした。6) Mo, W: Mo and W form a solid solution in the parent phase to reduce the rising motion velocity of dislocations, and effectively contribute to the improvement of strength even at a high temperature of 450 ° C. or higher. However, these elements have no effect when Mo + 1 / 2W is less than 0.5 wt%, and when added in excess of 2 wt%, Fe at high temperature.
The effect saturates to form a Laves phase, which is an intermetallic compound with. Therefore, the addition range is Mo
0.5 to 2 wt% at +1/2 W (preferably 0.5 to
1.5 wt%).
【００１５】７）Ｔａ，Ｈｆ，Ｚｒ，Ｏｓ：Ｔａ，Ｈ
ｆ，Ｚｒ及びＯｓはＭｏやＷと同じ効果があり、４５０
℃以上の高温でも強度の向上に有効に寄与する。これら
の元素は０．１ｗｔ％未満ではまったく効果がなく、ま
た４ｗｔ％を超えて添加してもその効果が飽和して意味
がないので、その添加範囲を０．１〜４ｗｔ％（望まし
くは０．５〜３．５ｗｔ％）とした。7) Ta, Hf, Zr, Os: Ta, H
f, Zr and Os have the same effect as Mo and W, and
It effectively contributes to the improvement of strength even at high temperatures of ℃ or more. If these elements are less than 0.1 wt%, there is no effect, and if added in excess of 4 wt%, the effect is saturated and meaningless, so the range of addition is 0.1 to 4 wt% (preferably 0%). 0.5 to 3.5 wt%).
【００１６】[0016]
【実施例】以下、具体的な実施例をあげ本発明の効果を
明らかにする。表１に示す成分組成からなる鋼を、溶解
−造塊−鍛造後、１０００℃、２０ｍｉｎの焼ならし、
７５０℃、３０ｍｉｎの焼戻しからなる熱処理を施し、
供試鋼を製造した。なお、このようにして得られた本発
明鋼の組織はいずれもフェライト内に大きさが数１０ｎ
ｍの微細な析出物が分散していた。EXAMPLES The effects of the present invention will be clarified below with reference to specific examples. After melting, ingot-forging, and normalizing steel having the composition shown in Table 1 at 1000 ° C. for 20 minutes,
Heat treatment consisting of tempering at 750 ° C for 30 min
The test steel was manufactured. The structures of the steels of the present invention thus obtained each have a size of several tens of nanometers in ferrite.
The fine precipitates of m were dispersed.
【００１７】これらの供試鋼について定荷重クリープ破
断試験を実施し、ラーソンミラーパラメータ法によって
４５０℃における１０5 ｈのクリープ破断強度を外挿し
た。結果を表１に併せて示す。比較例１，２はＪＩＳ
ＳＴＢ３４０相当材及び比較例３はＪＩＳ ＳＴＢ４１
０相当材である。比較例の４５０℃における１０5 ｈ外
挿クリープ破断強度はいずれも１０〜１１ｋｇｆ／ｍｍ
2 程度である。A constant load creep rupture test was carried out on these test steels, and the creep rupture strength of 10 5 h at 450 ° C. was extrapolated by the Larson Miller parameter method. The results are also shown in Table 1. Comparative Examples 1 and 2 are JIS
The material equivalent to STB340 and Comparative Example 3 are JIS STB41
It is a material equivalent to 0. All of the 10 5 h extrapolated creep rupture strengths at 450 ° C. of the comparative example are 10 to 11 kgf / mm.
It is about 2 .
【００１８】一方、本発明例Ｎｏ．１〜３に係わる材料
は、Ｎｂ及びＶの適量添加とＭｎの増加により、４５０
℃における１０5 ｈ外挿クリープ破断強度が比較鋼に対
し約４ｋｇｆ／ｍｍ2 程度向上している。さらに、本発
明例Ｎｏ．４はＢの少量添加により強度がさらに向上し
ている。また、本発明例Ｎｏ．５〜１３は固溶強化元素
であるＭｏ，Ｗ，Ｔａ，Ｈｆ，Ｚｒ，Ｈｆ及びＯｓの添
加により、４５０℃における１０5 ｈ外挿クリープ破断
強度が著しく向上している。On the other hand, the invention sample No. The materials related to Nos. 1 to 3 are 450 by adding an appropriate amount of Nb and V and increasing Mn.
The extrapolated creep rupture strength at 105 ° C for 10 5 h is improved by about 4 kgf / mm 2 relative to the comparative steel. Further, the present invention example No. In No. 4, the strength is further improved by adding a small amount of B. The invention example No. In Nos. 5 to 13, the addition of Mo, W, Ta, Hf, Zr, Hf, and Os, which are solid solution strengthening elements, significantly improves the 10 5 h extrapolated creep rupture strength at 450 ° C.
【００１９】[0019]
【表１】 [Table 1]
【００２０】[0020]
【発明の効果】高温強度に優れた本発明鋼は発電プラン
ト・熱交換器等の高温環境下で使用される鋼管の寿命延
長及び鋼管の管厚を薄くできることによる低コスト化に
寄与する。INDUSTRIAL APPLICABILITY The steel of the present invention, which is excellent in high temperature strength, contributes to cost reduction by prolonging the life of a steel pipe used in a high temperature environment such as a power plant and a heat exchanger and by making the pipe thickness thin.
───────────────────────────────────────────────────── フロントページの続き (56)参考文献 特開 平８−104943（ＪＰ，Ａ) 特開 昭52−71326（ＪＰ，Ａ) 特開 平５−271858（ＪＰ，Ａ) 特開 平７−258789（ＪＰ，Ａ) (58)調査した分野(Int.Cl.7，ＤＢ名) C22C 38/00 - 38/60 ─────────────────────────────────────────────────── ─── Continuation of the front page (56) Reference JP-A-8-104943 (JP, A) JP-A 52-71326 (JP, A) JP-A 5-271858 (JP, A) JP-A 7- 258789 (JP, A) (58) Fields investigated (Int. Cl. 7 , DB name) C22C 38/00-38/60
Claims (5)
０．１５〜０．５ｗｔ％、Ｍｎ：０．４〜２ｗｔ％、Ｎ
ｂ：０．０１〜０．１ｗｔ％、Ｖ：０．０１〜０．３ｗ
ｔ％を含有し、残部がＦｅ及び不可避的不純物からな
り、母地中に微細な析出物が分散していることを特徴と
する高温強度に優れた炭素鋼。1. C: 0.01 to 0.1 wt%, Si:
0.15-0.5 wt%, Mn: 0.4-2 wt%, N
b: 0.01 to 0.1 wt%, V: 0.01 to 0.3 w
t% and the balance is Fe and inevitable impurities.
Ri, carbon steel fine precipitate in the mother ground has excellent high-temperature strength, characterized that you have dispersed.
５０ｐｐｍ以下含有してなることを特徴とする高温強度
に優れた炭素鋼。2. The carbon steel according to claim 1, which contains B in an amount of 50 ppm or less, which is excellent in high temperature strength.
及びＷの１種以上を含有し、その含有量がＭｏ＋１／２
Ｗで０．５〜２ｗｔ％の範囲であることを特徴とする高
温強度に優れた炭素鋼。3. The carbon steel according to claim 1 , wherein Mo
And one or more of W, and the content is Mo + 1/2
Carbon steel excellent in high-temperature strength, characterized in that it is in a range of 0.5 to 2 wt% in W.
ａ，Ｈｆ，Ｚｒ，Ｏｓのうち１種以上の合計含有量とし
て０．１〜４ｗｔ％含有してなることを特徴とする高温
強度に優れた炭素鋼。4. The carbon steel according to claim 1 , wherein T
Carbon steel excellent in high-temperature strength, characterized by containing 0.1 to 4 wt% as a total content of at least one of a, Hf, Zr, and Os.
項２〜４に示した補助添加材を２項目以上複合添加させ
てなることを特徴とする高温強度に優れた炭素鋼。5. The carbon steel according to claim 1, which is obtained by adding two or more of the auxiliary additives shown in claims 2 to 4 in combination, and is excellent in high temperature strength.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP00293897A JP3524708B2 (en) | 1997-01-10 | 1997-01-10 | Carbon steel with excellent high-temperature strength |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP00293897A JP3524708B2 (en) | 1997-01-10 | 1997-01-10 | Carbon steel with excellent high-temperature strength |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH10195593A JPH10195593A (en) | 1998-07-28 |
| JP3524708B2 true JP3524708B2 (en) | 2004-05-10 |
Family
ID=11543308
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP00293897A Expired - Fee Related JP3524708B2 (en) | 1997-01-10 | 1997-01-10 | Carbon steel with excellent high-temperature strength |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP3524708B2 (en) |
Families Citing this family (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US6299705B1 (en) * | 1998-09-25 | 2001-10-09 | Mitsubishi Heavy Industries, Ltd. | High-strength heat-resistant steel and process for producing high-strength heat-resistant steel |
| JP4640775B2 (en) | 2004-11-25 | 2011-03-02 | キヤノンファインテック株式会社 | Heat fixing device and image forming apparatus |
-
1997
- 1997-01-10 JP JP00293897A patent/JP3524708B2/en not_active Expired - Fee Related
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