JPS5989752A - Welded structure of 12cr steel - Google Patents
Welded structure of 12cr steelInfo
- Publication number
- JPS5989752A JPS5989752A JP19892282A JP19892282A JPS5989752A JP S5989752 A JPS5989752 A JP S5989752A JP 19892282 A JP19892282 A JP 19892282A JP 19892282 A JP19892282 A JP 19892282A JP S5989752 A JPS5989752 A JP S5989752A
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- steel
- welded structure
- welding
- strength
- creep rupture
- Prior art date
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Abstract
Description
【発明の詳細な説明】
〔発明の利用分野〕
本発明は１２０ｒ系鋼溶接構造物に係シ、特に１２Ｃｒ
系高温用蒸気タービンケーシングの継手溶接及び補修溶
接における高温強度及び耐溶接割れ感受性を高めた溶接
構造物に関する。DETAILED DESCRIPTION OF THE INVENTION [Field of Application of the Invention] The present invention relates to welded structures of 120R series steel, particularly 12Cr welded structures.
The present invention relates to a welded structure with improved high-temperature strength and weld cracking susceptibility in joint welding and repair welding of high-temperature steam turbine casings.
従来の蒸気タービンは蒸気温度最大５６６Ｃ。 Conventional steam turbines have a maximum steam temperature of 566C.
蒸気圧力最大２４６ａｔｇであり、第１図に示すケーシ
ング不休１及び加減弁ケーシング２、及び第２図に示す
主蒸気弁ケーシング材３としてはＣｒ−ＭＯ−ｖ−鋼が
用いられ、これらの部材の継手溶接及び補修溶接（ｉＷ
接位置を第２図中、４で示す）にはＣｒ−ＭＯ系溶接棒
が用いられている。The maximum steam pressure is 246 atg. Joint welding and repair welding (iW
A Cr-MO type welding rod is used at the contact position (indicated by 4 in FIG. 2).
最近、石油、石炭などの化石燃料のコストが上昇を続け
ておシ、これら化石燃料を用いている火力プラントの発
電効率が重要になっている。発電効率を上げるためには
蒸気タービンの蒸気温度又は圧力な上げる必要がある。Recently, as the cost of fossil fuels such as oil and coal continues to rise, the power generation efficiency of thermal power plants that use these fossil fuels has become important. In order to increase power generation efficiency, it is necessary to increase the steam temperature or pressure of the steam turbine.
このよう字高効率タービン用材料としては上記した現用
タービン材料では強度不足である。更にそれに不随して
、それらの構造溶接及び補修溶接用として使用されてい
る溶着金属も強度不足で、高強度溶接材料が必要である
。The above-mentioned current turbine materials lack strength as materials for such high-efficiency turbines. Further, the weld metal used for structural welding and repair welding is insufficient in strength, and high-strength welding materials are required.
そのため、高効率タービンケーシング用としての強度を
有し、かつこのケーシング用溶着金属も高いクリープ破
断強度を有するとともに、溶接作業性の良好のものが要
望されていた。Therefore, there has been a demand for a weld metal for use in high-efficiency turbine casings, which also has high creep rupture strength and has good welding workability.
本発明の目的は、５５０〜６００Ｃにおいて高いクリー
プ破断強度を有し、又溶接工程における耐溶接割れ感受
性が低く、溶接作業性も極めて良好な１２Ｃｒ系鋼溶接
構造物を提供するものである。An object of the present invention is to provide a 12Cr steel welded structure that has high creep rupture strength at 550 to 600C, low susceptibility to weld cracking during the welding process, and extremely good welding workability.
本発明者らは、高効率タービンケーシング材として高温
強度、クリープ破断特性及び溶接割れ感受特性等の面か
ら、１２０ｒ系耐熱鋼が適用可能であることを見い出し
た。しかしこの１２Ｃｒ系耐熱鋼に対する溶接材料とし
て既存の溶接棒ではクリープ破断強度が不足で適用でき
ないことが明・らかとなシ、１２Ｃｒ系耐熱鋼に対し溶
接性を損わずクリープ破断強度に優れた溶接材料に到達
した。The present inventors have discovered that 120R heat-resistant steel is applicable as a high-efficiency turbine casing material in terms of high-temperature strength, creep rupture properties, weld crack sensitivity properties, and the like. However, it is clear that existing welding rods cannot be used as welding materials for this 12Cr heat-resistant steel due to insufficient creep rupture strength. Reached the welding material.
本発明は、このような知見に基づいてなされたものであ
って、第１の発明は１２Ｃｒ系耐熱駒または鍛鋼の溶接
構造物において、重量比でＣ：０．０５〜０．２％、８
ｉ：０．０５〜１％＃ Ｍｎ ：０．１〜１． Ｎｉ：
１．５％以下、Ｃｒ：９〜１３％。The present invention has been made based on such knowledge, and the first invention is a welded structure of a 12Cr heat-resistant piece or forged steel, in which C: 0.05 to 0.2% by weight, 8
i: 0.05-1% #Mn: 0.1-1. Ni:
1.5% or less, Cr: 9-13%.
ＭＯ：０．５〜２％、Ｎｂ：０．０５〜０．４％、Ｗ：
０．０５〜０．８％を含み、残部を鉄及び不可避不純物
からなり、Ｃｒ当量が１０以下である１２Ｃｒ系鋼溶接
構造物であり、第２の発明は１２Ｃｒ系鋳鋼または鍛鋼
を被溶接材とする溶接構造物において１．＊ｉ比でＣ：
０．０５〜０．２％、ｓｉ：ｏ、ｏｓ〜１． Ｍｎ ：
ｏ、ｘ−ｘ、 Ｎｉ ： １．５％以下、Ｃｒ：９〜
１３％、ＭＯ：０．５〜２％、Ｎｂ：０．０５〜０．４
％、Ｎ：０．０２〜０．１％、およびＷ：０．０５〜０
．８％を含み、残部鉄及び不６工避不純物元素からなシ
、Ｃｒ当量がｌθ以下である１２０ｒ系鋼溶接構造物で
ある。MO: 0.5-2%, Nb: 0.05-0.4%, W:
0.05 to 0.8%, the remainder is iron and unavoidable impurities, and the Cr equivalent is 10 or less. In a welded structure with 1. *C in i ratio:
0.05-0.2%, si:o, os-1. Mn:
o, x-x, Ni: 1.5% or less, Cr: 9~
13%, MO: 0.5-2%, Nb: 0.05-0.4
%, N: 0.02-0.1%, and W: 0.05-0
．． This is a welded structure of 120r steel having a Cr equivalent of lθ or less.
本発明において、上記の必須元素の池に脱酸及び結晶粒
微細化元素を単独又は複合で０．１％を含み、更に強度
増加元素■を０．５％以下含むこともできる。ここで脱
酸及び結晶粒微細化元素としては％ Ｚｒ、Ｍｇ及びＴ
ｉが望ましい。更に溶着金属中の元素のき有量の調整は
溶接心線またはフラックスから行なってもよい。In the present invention, the above-mentioned essential elements include 0.1% of deoxidizing and grain refining elements singly or in combination, and 0.5% or less of strength-increasing element (2) may also be included. Here, the deoxidizing and grain refining elements are % Zr, Mg and T.
i is preferable. Furthermore, the amount of elements in the weld metal may be adjusted from the weld core or flux.
本発明の溶接構造における溶着金属は主にマルテンサイ
ト組織を有するものでなければならない。The deposited metal in the welded structure of the present invention must primarily have a martensitic structure.
マルテンサイト組織は焼もどしマルテンサイト組織が好
ましく、高温において高強度を有する。化学組成及び熱
処理によってはフェライト組織が生じるので実質的にフ
ェライトが析出しないように全マルテンサイト組織とす
ることが最も有効である。フェライト組織の生成を防止
し、主としてマルテンサイト組織とするための化学組成
上Ｃｒ当量を１０以下とすることが必要である。The martensitic structure is preferably a tempered martensitic structure, which has high strength at high temperatures. Since a ferrite structure may occur depending on the chemical composition and heat treatment, it is most effective to form a completely martensitic structure so that substantially no ferrite precipitates. It is necessary to set the Cr equivalent to 10 or less in terms of chemical composition in order to prevent the formation of a ferrite structure and create a mainly martensitic structure.
Ｃｒ当量は以下の式で示される。The Cr equivalent is expressed by the following formula.
Ｃｒ当量ニー４０×Ｃ％−３０ＸＮ％−２ＸＭｎ％−４
ＸＮｉ％十Ｃｒ％＋６ｘＳｉ％＋４ＸＭＯ％＋１．５ｗ
％＋ＩＩＸＶ％＋５ＸＮｂ％
次に本発明における添加元素量の限定理由について説明
する。なお％はすべで重量％を示す。Cr equivalent knee 40×C%-30XN%-2XMn%-4
XNi%10Cr%+6xSi%+4XMO%+1.5w
%+IIXV%+5XNb% Next, the reason for limiting the amount of added elements in the present invention will be explained. Note that all percentages indicate weight percent.
Ｃは０．０５％以上において、クリープ破断強度を得る
ために必要な元素であるが、その量が０．２０％を越え
ると、高温に長時間さらされた場合、組織が不安定とな
υ長時間クリープ破断強度を低下させ、更に溶接工程に
おける溶接部の割れ感受性を高めるので０．０５〜０８
２％にしなければならない。特に０．０７〜０．１５％
が好ましい。C is an element necessary to obtain creep rupture strength at 0.05% or more, but if the amount exceeds 0.20%, the structure becomes unstable when exposed to high temperatures for a long time. 0.05 to 08 because it reduces the long-term creep rupture strength and further increases the cracking susceptibility of the welded part during the welding process.
It has to be 2%. Especially 0.07-0.15%
is preferred.
Ｓｉ及びＭｎは脱酸剤として添加するものであり、少量
の添加で十分効果は達成される。多量の添加は焼もどし
脆化感受性を高める。そのためには５ｉｔ−０，０５〜
１％及びＭｎ０．１〜１％にしなければならない。特に
Ｓｉは０．２〜０．５％及びＭｎは０．３〜０．７％が
好ましい。Si and Mn are added as deoxidizing agents, and a sufficient effect can be achieved by adding a small amount. Addition of a large amount increases susceptibility to tempering embrittlement. For that purpose, 5it-0,05～
1% and Mn 0.1-1%. In particular, Si is preferably 0.2 to 0.5% and Mn is preferably 0.3 to 0.7%.
Ｃｒは高温強度及び高温耐食性を高めるものであシ、高
温材料としては欠くことができない元素で９％以上必要
である。しかし、１３％を超えるとδフェライトが析出
し、クリープ破断強度、靭性及び疲労強度を著しく低下
させる。特に１０〜１１％の範囲が好しい。Cr increases high-temperature strength and high-temperature corrosion resistance, and is an indispensable element for high-temperature materials, and is required in an amount of 9% or more. However, if it exceeds 13%, δ ferrite will precipitate, significantly reducing creep rupture strength, toughness and fatigue strength. Particularly preferred is a range of 10 to 11%.
Ｎｉは高温強度及び靭性を高める元素であるが、１５％
を超えると、組織の変能点を下げ、組織が不安定となり
、クリープ破断強度を低下させるので、１．５％以下で
なければならない。特にＯ９３〜０．７％が好ましい。Ni is an element that increases high temperature strength and toughness, but at 15%
If it exceeds 1.5%, the inflection point of the structure will be lowered, the structure will become unstable, and the creep rupture strength will be lowered, so it must be 1.5% or less. Particularly preferred is O93 to 0.7%.
ＭＯは同浴強化及び析出硬化作用によってクリープ強度
を改善し、更に焼もどし脆化を防止する元素であるが、
０，５％未満ではその効果は不十分であシ、２％を超え
てもそれ以上の効果がなく飽和する。したがってＭＯは
０．５〜２％の範囲が有効である。特に０．９〜１．３
％の範囲が最も有効である。MO is an element that improves creep strength through bath strengthening and precipitation hardening effects, and also prevents tempering embrittlement.
If it is less than 0.5%, the effect is insufficient, and if it exceeds 2%, there is no further effect and the effect is saturated. Therefore, MO is effective in a range of 0.5 to 2%. Especially 0.9-1.3
A range of % is most useful.
Ｎｂは高温強度を高めるのに非常に効果的な元素である
。また、結晶粒径の微細化にも顕著に作用するが、この
ためには０．０５％以上必要とする。Nb is a very effective element for increasing high temperature strength. It also has a significant effect on making the crystal grain size finer, and for this purpose 0.05% or more is required.
一方、０．４％以上を超えるとフェライトの析出を促進
し、高温強度及び靭性を低下させる。したがって０．０
５〜０．４％の範囲でなければならない。On the other hand, when it exceeds 0.4%, precipitation of ferrite is promoted and high temperature strength and toughness are reduced. Therefore 0.0
Must be in the range 5-0.4%.
特に０．０８〜０．２％が最も有効である。In particular, 0.08 to 0.2% is most effective.
Ｎはクリープ破断強度の改善及びフェライトの析出防止
に効果があるが、０．０２％未満ではその効果が十分で
な（，０，１０％を超えるとクリープ破断強度を低下さ
せてしまうので好ましくない。N is effective in improving creep rupture strength and preventing the precipitation of ferrite, but if it is less than 0.02%, the effect is insufficient (if it exceeds 0.10%, the creep rupture strength will decrease, so it is not preferable. .
特に０．０４〜０．０６％が好ましい。Particularly preferred is 0.04 to 0.06%.
Ｗは微量で顕著に高温強度を高める。０．０５％未満で
は効果が少なく、また０、８％を超えると急激に強度を
低下させる。Ｗｆｌｏ、１〜０，８％以下とすべきであ
る。一方、Ｗは０．５％を超えると著しく、靭性を低め
るので、高靭性が必要な部材では０．５％未満とするの
が好ましい。特に０．２〜０．４％が好ましい。Even a small amount of W significantly increases high temperature strength. If it is less than 0.05%, the effect will be small, and if it exceeds 0.8%, the strength will decrease rapidly. Wflo should be less than 1-0.8%. On the other hand, when W exceeds 0.5%, the toughness is significantly lowered, so it is preferably less than 0.5% for members requiring high toughness. Particularly preferred is 0.2 to 0.4%.
上記の必須元素の他に焼入性強化元素としてｖ１脱酸及
び結晶粒径微細化元素としてＺｒ、Ｍｇ及びＴＩをそれ
ぞれ添加してもよい。In addition to the above-mentioned essential elements, Zr, Mg, and TI may be added as v1 deoxidizing elements to strengthen hardenability and as elements to refine grain size.
■は焼入性強化元素で、元素と結合して炭化物を形成し
、クリープ破断強度を高める。その効果は０．５０％以
下で十分である。逆に０．５％を越えると溶接割れ感受
性を著しく高めるので０．５％以下で十分である。特に
０．１〜０．３の範囲が有効である。(2) is a hardenability-strengthening element that combines with other elements to form carbides and increases creep rupture strength. The effect is sufficient at 0.50% or less. On the other hand, if it exceeds 0.5%, the weld cracking susceptibility increases significantly, so 0.5% or less is sufficient. A range of 0.1 to 0.3 is particularly effective.
７、 ｒ、 ＩＩＩ ｉ及びＭｇは溶接金属中の脱酸及
び結晶粒径の微細化を促進する元素であり、単独で０．
１％以下又は複合でも０．１％以下でその効果は十分達
成される。それ以上の添加は高温強度及び靭性を低下さ
せる。特に単独又は複合でも０．０３〜０，０６％が好
ましい。7.r, IIIi and Mg are elements that promote deoxidation in the weld metal and refinement of crystal grain size, and 0.
The effect can be fully achieved at 1% or less, or even at 0.1% or less in combination. Addition of more than that will reduce high temperature strength and toughness. In particular, 0.03 to 0.06% is preferable, either alone or in combination.
このような溶着金属は、１２０ｒ系鋳鋼または第１表に
示す被溶接材の熱処理例を第２光に示す。Examples of heat treatment of such weld metals, such as 120r cast steel or materials to be welded shown in Table 1, are shown in the second light.
第 ２ 表 ※２回くシ返しが望しい。Table 2 *It is recommended to repeat the process twice.
心線は真空溶解で溶製し、熱処理及び鍛造後、伸線加工
によシ直径４ｗｓ、長さ４００ｍｍに加工しプはライム
系である。第３表の心線は用いて低水素型被懐アーク溶
接棒とした。The core wire is made by vacuum melting, and after heat treatment and forging, it is drawn to a diameter of 4 ws and a length of 400 mm.The wire is made of lime. The core wires shown in Table 3 were used to make low-hydrogen arc covered welding rods.
第 ５ 表
第６表は本発明の溶接棒と比較のために用いた市販の１
２Ｃｒ系高温用被覆アーク溶接棒（直径４、０ ｍ ）
の溶着金属の化学組成を示す。Table 5 Table 6 shows the welding rod of the present invention and the commercially available one used for comparison.
2Cr-based high-temperature coated arc welding rod (diameter 4.0 m)
The chemical composition of the weld metal is shown below.
第 ６ 表
ド１
匣１
使用した供試母材は第７表に示す化学組成からなる１２
Ｃ「系高温用耐熱鋳鋼を用いた。Table 6 Box 1 The test base material used had the chemical composition shown in Table 7.
C: Uses high-temperature heat-resistant cast steel.
第 ７ 表
実施例の溶接施工条件を第３図に示す。予熱温度２００
〜２５０Ｃで十分母材を加熱後、パス間温度及び後熱開
始温度２０（ｌ後、４００Ｃで３０分間の後熱保持後８
０Ｃまで冷却し、その後７００Ｃで４時間保持のＳＲ処
理を施した。Table 7 The welding conditions for the examples are shown in Figure 3. Preheating temperature 200
After sufficiently heating the base material at ~250C, the inter-pass temperature and after-heating start temperature of 20 (l), and after holding the after-heating at 400C for 30 minutes, 8
It was cooled to 0C, and then subjected to SR treatment at 700C for 4 hours.
溶接棒の溶接割れ感受性を検討するために溶接拘束割れ
試験を実施した。試験片の形状はＪＩＳＺ３１５７のＵ
型溶接われ試験片に準じた。板厚はａＯ，、である。Weld restraint cracking tests were conducted to examine the welding cracking susceptibility of welding rods. The shape of the test piece is JIS Z3157 U.
Same as type welded test piece. The plate thickness is aO,.
第８表及び第９表は、それぞれ第３表及び第４表の比較
溶接棒溶着金属及び本発明の引張強さ、衝撃値及び６０
０Ｃ，１０’時間クリープ破断強度及び溶接部断面割れ
率を示す。Tables 8 and 9 show the tensile strength, impact value and 60
0C, 10' hour creep rupture strength and weld section cross-sectional crack rate are shown.
第 ８ 表
第 ９ 表
次の通シである。Ｎ添加の有無にかかわらず、高Ｎｂ（
第８表及び第９表のＡＩ）及び高Ｎｂ（第８表及び第９
表の４２）の衝撃値は、両者共比較材よシも低い値を示
す。Ｎｂ含有量がＡＸ〜とＡ２の中間（第８表のＡｌｌ
および第９表のＡ７）では衝撃値は比較材よシもＩ Ｋ
ｒ／ｃ＆高い値を示している。一方、クリープ破断強度
は高Ｎｂ、低Ｎｂの場合とも比較材と同程度であるが、
第８表の墓１１及び第９表のＪＩ６７は比較材よシも約
３Ｋｆ／１ｍ”高い値を示す。Tables 8 and 9 are as follows. High Nb (
AI in Tables 8 and 9) and high Nb (AI in Tables 8 and 9)
The impact value of item 42) in the table is lower than that of the comparative material. The Nb content is between AX~ and A2 (All in Table 8)
And in A7) of Table 9, the impact value is lower than that of the comparative material.
It shows a high value of r/c&. On the other hand, the creep rupture strength is similar to that of the comparative material in both high Nb and low Nb cases;
Grave 11 in Table 8 and JI67 in Table 9 show values that are approximately 3 Kf/1m" higher than the comparative materials.
これらの試験結果は、Ｃｒ当量が１０を超えると、フェ
ライトが生成するため靭性及び高温強度が低下する。し
かしＮｂが少すぎる場合、Ｎｂ特有の組織の微細化及び
高温で安定なＮｂ炭化物の生成がないためＮｂの効果が
発揮されない。第８表（７）Ａｌｌ及び第９表（７）Ａ
７ｔｊ：Ｃｒ当量が１０以下であり、しかもＮｂの適正
な添加量による組織の微細化効果によシ高温強度及び靭
性が改善され次ものである。These test results show that when the Cr equivalent exceeds 10, toughness and high-temperature strength decrease due to the formation of ferrite. However, if the amount of Nb is too small, the effect of Nb will not be exhibited because there will be no refinement of the structure peculiar to Nb and no formation of Nb carbide which is stable at high temperatures. Table 8 (7) All and Table 9 (7) A
7tj: The Cr equivalent is 10 or less, and the high-temperature strength and toughness are improved due to the refinement of the structure due to the appropriate addition amount of Nb.
第８表のＡ３及びＡ ４ 、第９表のＡ３はいずれもＭ
Ｏの添加による効果をみたものであシ、いずれもＭＯの
適正添加量範囲外であるため、靭性及びクリープ破断強
度は比較材よりも低い。第８表及び第９表のＡ３は、い
ずれもＣｒ当量が高すぎるため、フェライトが生成しク
リープ破断強度及び靭性が著しく低い。A3 and A 4 in Table 8 and A3 in Table 9 are both M
This study examined the effect of adding O, and since both amounts were outside the appropriate addition amount range of MO, the toughness and creep rupture strength were lower than the comparative materials. In both A3 in Tables 8 and 9, the Cr equivalent was too high, so ferrite was formed and the creep rupture strength and toughness were extremely low.
第８表のＡ５及び第９表のＡ４は、いずれも本発明の組
成であって、特に■を微°量とし、■含有。A5 in Table 8 and A4 in Table 9 both have the compositions of the present invention, especially containing a very small amount of ■.
量の減少分をＣによって補なっておシ、比較材よシも高
い靭性及びクリープ破断強度が高い。The decrease in the amount of carbon was compensated for by C, and the material had higher toughness and creep rupture strength than the comparative material.
第８表の４６及び第９表のＡ５は、Ｃの含有量が多いた
めに焼入性を増し、溶着金属の硬さが高いためクリープ
破断強度は比較材よりも高いが、靭性は著しく低い。46 in Table 8 and A5 in Table 9 have a high C content, which increases hardenability, and the hardness of the weld metal is high, so the creep rupture strength is higher than the comparative materials, but the toughness is significantly lower. .
第８表の４７では、Ｃｒ当量が高く７エ２イトの生成が
あるため、比較材よシも靭性及びクリープ破断強度が低
い。第８表のＡ８および第９表のＡ６は、Ｗ含有量が低
いため靭性は比較材よシも高いが、炭化物の凝集、粗大
化現象低減の効果がなくなシ、炭化物の粗大化が起り、
クリープ破断強度が低くなっている。Sample 47 in Table 8 has a high Cr equivalent and the formation of 7E2ite, so its toughness and creep rupture strength are low compared to the comparative materials. A8 in Table 8 and A6 in Table 9 have higher toughness than the comparative materials due to their low W content, but the effect of reducing carbide agglomeration and coarsening phenomenon is lost, and carbide coarsening occurs. ,
Creep rupture strength is low.
第８表のＡ９は低Ｃ１高Ｗの場合であるがＣｒ当量が１
０以上であり、フェライトが生成し、特にクリープ破断
強度が低い。A9 in Table 8 is a case of low C1 high W, but the Cr equivalent is 1
0 or more, ferrite is generated, and the creep rupture strength is particularly low.
第８表のＡ１０およびＡｌｌ、第９表のＡ７の本発明の
組成範囲内であシ、いずれも比較材よシも靭性及びクリ
ープ破断強度が高い。Both A10 and All in Table 8 and A7 in Table 9 are within the composition range of the present invention, and both have higher toughness and creep rupture strength than the comparative materials.
次に割れ試験結果についてみると、溶接施工条件は第３
図に示すととくであシ、１パス溶接によって行った。割
れ発生の有無は試験ビードを６断面に分割し、光学顕微
鏡により観察し調査した、第８表および第９表の断面割
れ率は６断面の溶接割れ率の平均値を示す。その結果、
割れは第８表のＡ６および第９表のＡ５の高Ｃ１及び高
Ｖに発生したが、本発明材の第８表のＡ５，１０及び１
１および第９表のＡ４．Ａ７には割れは認められなかっ
た。Next, looking at the cracking test results, welding construction conditions were
As shown in the figure, one-pass welding was performed. The presence or absence of cracking was investigated by dividing the test bead into 6 cross sections and observing them using an optical microscope. The cross-sectional crack rates in Tables 8 and 9 indicate the average value of the weld crack rates of the 6 cross sections. the result,
Cracking occurred in high C1 and high V of A6 in Table 8 and A5 in Table 9, but cracks occurred in A5, 10 and 1 of Table 8 of the invention material.
1 and A4 in Table 9. No cracks were observed in A7.
以上のように本発明の溶接構造物は、高温強度及び靭性
が高く、更に耐溶接割れ感受性も良好であシ、特に６０
０？、ｔでの高温クリープ破断強度は著しく高く、高効
率蒸気タービンケーシング用溶接材として要求される強
度を十分満足していることが明らかであり、５５０〜６
００Ｃでの高効率磁気タービンケーシング用溶接構造と
して好適である。As described above, the welded structure of the present invention has high high-temperature strength and toughness, and also has good weld cracking resistance.
0? It is clear that the high-temperature creep rupture strength at , t is extremely high and satisfies the strength required as a welding material for high-efficiency steam turbine casings;
It is suitable as a welded structure for high efficiency magnetic turbine casing at 00C.
【図面の簡単な説明】
第１図は蒸気タービンケーシング本体、蒸気加減弁ケー
シングの断面構成図、第２図は主蒸気ケーシング及びそ
の溶接部の断面構成図、第３図は実施例で用いた溶接施
工の説明図である。
１・・・ケーシング本体、２・・・加減弁ケーシング、
３・・・主蒸気弁ケーシング、４・・・溶接部。[Brief explanation of the drawings] Figure 1 is a cross-sectional diagram of the steam turbine casing body and steam control valve casing, Figure 2 is a cross-sectional diagram of the main steam casing and its welded parts, and Figure 3 is the cross-sectional diagram of the main steam casing and its welded parts. It is an explanatory view of welding construction. 1...Casing body, 2...Adjustment valve casing,
3... Main steam valve casing, 4... Welded part.
Claims (2)
造において、重量比でＣ：０．０５〜０．２％。 ＳＩ 二 ０．０５ 〜ｉ ％、Ｍｎ：０．１ 〜
ｌ ％、 Ｎ ｊ：１．５％以下、Ｃｒ：９．０〜
１３％、Ｍｏ：ｏ、５〜２％、 Ｎ ｂ ： ０．０５
〜０．４％、 Ｗ ： ０．０５〜０．８％を含み、残
部鉄及び不可避不純物元素がらなシ、Ｃ「当量が１０以
下であることを特徴とする１２０ｒ系鋼溶接構造物。1. In a welded structure in which the material to be welded is 12Cr cast steel or forged steel, C: 0.05 to 0.2% by weight. SI2 0.05~i%, Mn:0.1~
l%, Nj: 1.5% or less, Cr: 9.0~
13%, Mo:o, 5-2%, Nb: 0.05
~0.4%, W: 0.05~0.8%, and the balance is iron and unavoidable impurity elements.
造物において、重量比でＣ：０．０５〜０．２％、Ｓｉ
：０．０５〜１％、Ｍｎ：０．１〜１％。 Ｎｔ：ｘ、ｓ％以下、Ｃｒ：９゜０〜１３％、ＭＯ：０
、５〜２％、 Ｎｂ ： ０．０５〜０．４％と、Ｎ：
０．０２〜０．１％およびｗ：ｏ、ｏｓ〜０．８％を含
み残部鉄−及び不可避不純物元素からなシ、Ｃｒ当量が
１０以下であることを特徴とする１２０ｒ系鋼溶接構造
物。2.12Cr-based cast steel or forged steel is used as the welding material for welded structures, with a weight ratio of C: 0.05 to 0.2%, Si
:0.05-1%, Mn:0.1-1%. Nt: x, s% or less, Cr: 9° 0-13%, MO: 0
, 5-2%, Nb: 0.05-0.4%, N:
A 120R series steel welded structure characterized by containing 0.02 to 0.1% and w:o, os to 0.8%, the balance being iron and inevitable impurity elements, and having a Cr equivalent of 10 or less .
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP19892282A JPS5989752A (en) | 1982-11-15 | 1982-11-15 | Welded structure of 12cr steel |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP19892282A JPS5989752A (en) | 1982-11-15 | 1982-11-15 | Welded structure of 12cr steel |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPS5989752A true JPS5989752A (en) | 1984-05-24 |
Family
ID=16399186
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP19892282A Pending JPS5989752A (en) | 1982-11-15 | 1982-11-15 | Welded structure of 12cr steel |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS5989752A (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH08231092A (en) * | 1995-02-28 | 1996-09-10 | Negishi Seisakusho:Kk | Fixing device for rolling end part of long-sized sheet |
Citations (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS56116858A (en) * | 1980-02-20 | 1981-09-12 | Toshiba Corp | Steam turbine rotor |
| JPS57120654A (en) * | 1981-01-16 | 1982-07-27 | Toshiba Corp | Heat resistant 12% cr steel |
| JPS57120655A (en) * | 1981-01-16 | 1982-07-27 | Toshiba Corp | Moving vane of steam turbine |
| JPS5837159A (en) * | 1981-08-26 | 1983-03-04 | Hitachi Ltd | Heat resistant martensite steel |
| JPS58110662A (en) * | 1981-12-25 | 1983-07-01 | Hitachi Ltd | Heat resistant steel |
| JPS58110661A (en) * | 1981-12-25 | 1983-07-01 | Hitachi Ltd | Heat resistant steel |
| JPS58120764A (en) * | 1982-01-08 | 1983-07-18 | Toshiba Corp | Moving vane of steam turbine with superior strength at high temperature and low creep crack propagating speed |
-
1982
- 1982-11-15 JP JP19892282A patent/JPS5989752A/en active Pending
Patent Citations (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS56116858A (en) * | 1980-02-20 | 1981-09-12 | Toshiba Corp | Steam turbine rotor |
| JPS57120654A (en) * | 1981-01-16 | 1982-07-27 | Toshiba Corp | Heat resistant 12% cr steel |
| JPS57120655A (en) * | 1981-01-16 | 1982-07-27 | Toshiba Corp | Moving vane of steam turbine |
| JPS5837159A (en) * | 1981-08-26 | 1983-03-04 | Hitachi Ltd | Heat resistant martensite steel |
| JPS58110662A (en) * | 1981-12-25 | 1983-07-01 | Hitachi Ltd | Heat resistant steel |
| JPS58110661A (en) * | 1981-12-25 | 1983-07-01 | Hitachi Ltd | Heat resistant steel |
| JPS58120764A (en) * | 1982-01-08 | 1983-07-18 | Toshiba Corp | Moving vane of steam turbine with superior strength at high temperature and low creep crack propagating speed |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH08231092A (en) * | 1995-02-28 | 1996-09-10 | Negishi Seisakusho:Kk | Fixing device for rolling end part of long-sized sheet |
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