JPS596743B2 - Welding method - Google Patents
Welding methodInfo
- Publication number
- JPS596743B2 JPS596743B2 JP5550175A JP5550175A JPS596743B2 JP S596743 B2 JPS596743 B2 JP S596743B2 JP 5550175 A JP5550175 A JP 5550175A JP 5550175 A JP5550175 A JP 5550175A JP S596743 B2 JPS596743 B2 JP S596743B2
- Authority
- JP
- Japan
- Prior art keywords
- stainless steel
- welding
- overlay
- metal
- overlay metal
- 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
Links
- 238000003466 welding Methods 0.000 title claims description 36
- 238000000034 method Methods 0.000 title claims description 16
- 229910052751 metal Inorganic materials 0.000 claims description 40
- 239000002184 metal Substances 0.000 claims description 40
- 239000010935 stainless steel Substances 0.000 claims description 26
- 229910001220 stainless steel Inorganic materials 0.000 claims description 26
- 239000000463 material Substances 0.000 claims description 14
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims description 12
- 229910052799 carbon Inorganic materials 0.000 claims description 12
- 229910000831 Steel Inorganic materials 0.000 claims description 7
- 239000010959 steel Substances 0.000 claims description 7
- 150000002739 metals Chemical class 0.000 claims 1
- 238000010438 heat treatment Methods 0.000 description 11
- 238000001556 precipitation Methods 0.000 description 9
- 239000011651 chromium Substances 0.000 description 7
- 150000001247 metal acetylides Chemical class 0.000 description 7
- 238000000137 annealing Methods 0.000 description 6
- 239000010955 niobium Substances 0.000 description 6
- 230000035882 stress Effects 0.000 description 6
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 description 5
- 239000011159 matrix material Substances 0.000 description 5
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 description 4
- 229910052804 chromium Inorganic materials 0.000 description 4
- 229910000859 α-Fe Inorganic materials 0.000 description 4
- 229910001566 austenite Inorganic materials 0.000 description 3
- 230000007797 corrosion Effects 0.000 description 3
- 238000005260 corrosion Methods 0.000 description 3
- 238000005336 cracking Methods 0.000 description 3
- 229910000975 Carbon steel Inorganic materials 0.000 description 2
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 2
- 239000010962 carbon steel Substances 0.000 description 2
- 230000007423 decrease Effects 0.000 description 2
- 238000010586 diagram Methods 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 239000007789 gas Substances 0.000 description 2
- 229910052739 hydrogen Inorganic materials 0.000 description 2
- 239000001257 hydrogen Substances 0.000 description 2
- 239000002689 soil Substances 0.000 description 2
- 230000008646 thermal stress Effects 0.000 description 2
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 description 1
- 101150000971 SUS3 gene Proteins 0.000 description 1
- 238000005452 bending Methods 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- UFGZSIPAQKLCGR-UHFFFAOYSA-N chromium carbide Chemical compound [Cr]#C[Cr]C#[Cr] UFGZSIPAQKLCGR-UHFFFAOYSA-N 0.000 description 1
- 238000007796 conventional method Methods 0.000 description 1
- 230000001771 impaired effect Effects 0.000 description 1
- 238000009434 installation Methods 0.000 description 1
- 229910000765 intermetallic Inorganic materials 0.000 description 1
- 229910052742 iron Inorganic materials 0.000 description 1
- 238000004519 manufacturing process Methods 0.000 description 1
- UNASZPQZIFZUSI-UHFFFAOYSA-N methylidyneniobium Chemical compound [Nb]#C UNASZPQZIFZUSI-UHFFFAOYSA-N 0.000 description 1
- 239000000203 mixture Substances 0.000 description 1
- 229910052750 molybdenum Inorganic materials 0.000 description 1
- 239000011733 molybdenum Substances 0.000 description 1
- 230000001737 promoting effect Effects 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
- 230000002195 synergetic effect Effects 0.000 description 1
- 229910003470 tongbaite Inorganic materials 0.000 description 1
Classifications
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K35/00—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting
- B23K35/001—Interlayers, transition pieces for metallurgical bonding of workpieces
- B23K35/004—Interlayers, transition pieces for metallurgical bonding of workpieces at least one of the workpieces being of a metal of the iron group
Landscapes
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Arc Welding In General (AREA)
Description
【発明の詳細な説明】
本発明は溶接方法に係るもので、特に高温高圧で使用し
かつ耐食性を必要とする圧力容器内面に別の器捲部品等
を取付けるための溶接方法の改善に関する。DETAILED DESCRIPTION OF THE INVENTION The present invention relates to a welding method, and more particularly to an improvement in a welding method for attaching other parts, etc. to the inner surface of a pressure vessel that is used at high temperatures and pressures and requires corrosion resistance.
一般に高温高圧ガスを取扱う圧力容器で、しかも水素ガ
ス雰囲気のもとで使用するものに耘いては、高温、高圧
下に耘ける強度的な要件を満足するものであることはも
ちろん、耐食性の面でも厳しい要件を満足することが要
求される。In general, pressure vessels that handle high-temperature, high-pressure gases and are used in hydrogen gas atmospheres must not only meet the strength requirements of being able to withstand high temperatures and high pressures, but also have corrosion resistance. However, they are required to meet strict requirements.
したがつてクローム（以下Ｃｒと記載）、モリブデン（
以下Ｍｏと記載）等を含む特殊鋼その他炭素鋼等の内面
に耐食性の優れたステンレス鋼を肉盛し、圧力容器を形
成しているのが普通である。このような溶接を行なつた
のち、溶接の際発生した応力を除去するため９焼鈍や、
高温、高圧のもとで使用することから必然的に高温に加
熱されることになるが、この際、溶接部と肉盛金属との
境界部に割れが発生する傾向がみられる。すなわち、応
力除去焼鈍（焼鈍温度は通常６５０〜７００℃）の際や
、あるいは４００℃以上の高温、高圧の条件のもとで使
用している際に、クローム系炭化物あるぃはσ相（クロ
ーム、鉄を主成分とした金属間化合物）などがδフェラ
イト相中から析出するために溶接部分等が脆化し、割れ
の発生する傾向がみられる。また高温、高圧ガス等を取
扱う圧力容器によつては、その内部に別の内部装置を取
付けることが必要である場合が多く、当該内部装置取付
けのための溶接に際してその溶接の熱サイクルのため脆
化がさらに促進され、上記のごとさ割れの発生がいよい
よ顕著となる事態が生ずる。第１図及び第２図は以上に
説明したような事情を示す説明図で、圧力容器等の母材
１（２れＣｒ−ｌＭｏ鋼を使用している例が多い）の内
表面にステンレス鋼ＳＵＳ３０９からなる肉盛金属２、
さらに別のステンレス鋼ＳＵＳ３４７肉盛金属３を肉盛
し、その上さらに内部装置４の一部を当該肉盛金属３の
上に溶接して取付けた状況を示したものである。この際
、当該内部装置４の一部は、溶接金続５（ＳＵＳ３４７
ステンレス鋼を用いることが多い）によつて上記肉盛金
属３の土に溶接され、取り付けられる場合が多く、当該
溶接金属５と、上記肉盛金属３との境界部分に肉盛溶接
金属３の脆化等に起因する割れ６の発生がみられ易いも
のである。また圧力容器等を水素ガス雰囲気中で使用す
る場合には、当該割れ６の直下の部分にある上記圧力容
器母材１（２ｋＣｒ−１Ｍ０鋼）が水素損傷を受け、こ
の面でも当該圧力容器の破損を促進することもあり、圧
力容器製作上の大きな問題となつている。上記で説明し
た割れ６は特に上記溶接金属５の端部であつてかつ上記
肉盛金属３と接する部分に発生し易いものである。また
上記のごとき内部装置４の取付けには一般に多層溶接を
行なうことが多く各層の溶接の熱サイクルによつて脆化
現象にさらに拍車がかかることにもなる。このような脆
化現象は、前記でも簡単に説明したように〜炭化物等の
析出、すなわち、高温割れを防止する目的で晶出させた
δフエライト相からのクローム系炭化物あるいはσ相の
析出とオーステナイト母相中に訃けるニオビウム炭化物
（以下ＮｂＣと記載する）析出の相乗効果によるもので
あり、肉盛金属２のＳＵＳ３Ｏ９系ステンレス鋼よりも
激しく脆化する。以上の観点から、溶接時あるいは溶接
後に寂ける前記のような脆化を防止する方法として、δ
フエライト相の量を少なくすることにより脆化原因の一
つである、Ｃｒ系炭化物あるいはσ相の析出を少なくす
る等の対策や配慮がとられているが、このような手段で
は溶接の施工がいろいろと面倒であり、また溶接熱サイ
クルに起因するような脆化の促進に対してはほとんど効
果がみられない。本発明は以上に説明したような従来技
術にみられる問題点に鑑みて提案するもので、特に水素
雰囲気のもとで使用する、高温高圧圧力容器の内部装置
を取付けるに際し、溶接後の熱処理、あるいは加熱サイ
クル等によつても溶接部に脆化がみられず、また溶接部
と微小なクラツクが発生しても圧力容器等の母材に対す
る水素損傷を少なくし得るような、改善された新規な溶
接方法に関するものである。Therefore, chromium (hereinafter referred to as Cr), molybdenum (
It is common to form a pressure vessel by overlaying stainless steel with excellent corrosion resistance on the inner surface of special steel, carbon steel, etc., including carbon steel (hereinafter referred to as Mo), etc. After performing such welding, 9 annealing is performed to remove the stress generated during welding.
Since it is used under high temperature and high pressure, it is inevitably heated to high temperatures, and at this time, there is a tendency for cracks to occur at the boundary between the weld and the overlay metal. In other words, during stress relief annealing (annealing temperature is usually 650 to 700°C) or when used under high temperature and high pressure conditions of 400°C or higher, chromium-based carbide or σ phase (chromium , iron-based intermetallic compounds) are precipitated from the δ ferrite phase, making welded parts brittle and prone to cracking. In addition, for pressure vessels that handle high temperature, high pressure gas, etc., it is often necessary to install another internal device inside the vessel, and when welding to install the internal device, the thermal cycle of the welding causes brittleness. As a result, the occurrence of the above-mentioned cracking becomes even more noticeable. Figures 1 and 2 are explanatory diagrams showing the situation explained above, in which stainless steel is used on the inner surface of the base material 1 (often made of Cr-1Mo steel) of pressure vessels, etc. Overlay metal 2 made of SUS309,
This figure shows a situation in which another stainless steel SUS347 overlay metal 3 is overlaid, and a part of the internal device 4 is further welded and attached onto the overlay metal 3. At this time, a part of the internal device 4 is made of weld metal 5 (SUS347
The overlay metal 3 is often welded and attached to the soil of the overlay metal 3 by using stainless steel (often stainless steel), and the overlay weld metal 3 is often welded to the soil of the overlay metal 3 at the boundary between the weld metal 5 and the overlay metal 3. Cracks 6 due to embrittlement are likely to occur. In addition, when a pressure vessel or the like is used in a hydrogen gas atmosphere, the pressure vessel base material 1 (2kCr-1M0 steel) located directly under the crack 6 suffers hydrogen damage, and in this respect, the pressure vessel is also damaged. This is a major problem in the production of pressure vessels, as it can accelerate damage. The above-described cracks 6 are particularly likely to occur at the ends of the weld metal 5 and in contact with the overlay metal 3. Furthermore, multi-layer welding is generally used to attach the internal device 4 as described above, and the thermal cycle of welding each layer further accelerates the embrittlement phenomenon. As briefly explained above, this embrittlement phenomenon is caused by the precipitation of carbides, etc., that is, the precipitation of chromium carbide or σ phase from the δ ferrite phase crystallized for the purpose of preventing hot cracking, and the precipitation of austenite. This is due to the synergistic effect of the precipitation of niobium carbide (hereinafter referred to as NbC) in the matrix, and the embrittlement is more severe than that of the SUS3O9 stainless steel of overlay metal 2. From the above points of view, as a method to prevent the above-mentioned embrittlement that occurs during or after welding, δ
Measures and considerations have been taken to reduce the precipitation of Cr-based carbides or σ phase, which is one of the causes of embrittlement, by reducing the amount of ferrite phase, but such measures do not allow welding. It is troublesome in many ways, and has little effect on promoting embrittlement caused by welding thermal cycles. The present invention is proposed in view of the problems seen in the prior art as explained above, and is particularly suitable for post-weld heat treatment and Or new and improved products that do not show embrittlement in the welded part even when subjected to heating cycles, etc., and can reduce hydrogen damage to base materials such as pressure vessels even if small cracks occur with the welded part. This relates to a welding method.
本発明になる新規な溶接方法は、内部装置等の溶接部直
下の肉盛金属に超低炭素のステンレス鋼を使用し、また
肉盛金属を：層盛りとしかつ溶接後の熱処理を省略する
ことを骨子とするものである。以下に訃いて、本発明に
なる溶接方法の実施例に基づき本発明についてさらに具
体的に説明する。前記ですでに説明したように、溶接部
に｝いて脆化が起こり、さらに加熱サイクルが加わるこ
と等によつて熱応力の発生にともなうクラツクが生成す
る原因としては、たとえばＳＵＳ３４７系ステンレス鋼
の場合、憎処理、加熱サイクル等によつて析出する炭化
物、あるいはσ相と、その他オーステナイト母材中に析
出するＮｂＣ等が主な原因であるとされている。The new welding method of the present invention uses ultra-low carbon stainless steel for the overlay metal directly under the welding part of internal devices, etc., and also uses a layered overlay metal and omit heat treatment after welding. The main points are as follows. The present invention will be described in more detail below based on examples of the welding method according to the present invention. As already explained above, embrittlement occurs in the welded part, and cracks are generated due to the generation of thermal stress due to heating cycles, for example, in the case of SUS347 stainless steel. The main causes are said to be carbides or σ phase precipitated by heat treatment, heating cycles, etc., and NbC precipitated in the austenite base material.
そこで溶接部に｝ける炭化物の生成、析出の主原因を断
つために母相金属中の炭素含有量を好ましくは０．０３
％以下にするとともに、Ｎｂの含有量もなるべく少なく
するように考慮したものである。第３図は本発明になる
溶接方法の実施例を示す説明図である。な｝図中、前出
の第１図｝よび第２図と同一の符号はそれぞれ同一の部
分、素材を示すものである。第３図に訃いて、圧力容器
母材１（２ｃｒ一１Ｍ０鋼）にＳＵＳ３Ｏ９系ステンレ
ス鋼肉盛金属２ＳＵＳ３４７系ステンレス鋼肉盛金属３
を肉盛し、さらに当該肉盛金属３の上に炭素含有量が０
．０３％以下の超低炭素ステンレス鋼ＳＵＳ３４７（以
下ＳＵＳ３４７−ＵＬＣと記載する）７を肉盛し、当該
ＳＵＳ３４７系ステンレス鋼肉盛金属３訃よび超低炭素
のステンレス鋼ＳＵＳ３４７−ＵＬＣ肉盛金属７の上に
圧力容器等の内部装置４の一部を溶接した状況が示さた
ている。Therefore, in order to eliminate the main cause of carbide formation and precipitation in the weld zone, the carbon content in the matrix metal is preferably 0.03.
% or less, and also to reduce the Nb content as much as possible. FIG. 3 is an explanatory diagram showing an embodiment of the welding method according to the present invention. } In the figures, the same reference numerals as those in FIG. 1 and FIG. 2 above indicate the same parts and materials, respectively. As shown in Figure 3, pressure vessel base material 1 (2CR-1M0 steel) is made of SUS3O9 stainless steel overlay metal 2SUS347 stainless steel overlay metal 3
is overlaid, and further on the overlay metal 3, the carbon content is 0.
．． 03% or less ultra-low carbon stainless steel SUS347 (hereinafter referred to as SUS347-ULC) 7, and the SUS347 series stainless steel overlay metal 3 and the ultra-low carbon stainless steel SUS347-ULC overlay metal 7. A situation in which a part of the internal device 4 such as a pressure vessel is welded is shown on the top.
当該内部装置４の一部は上記肉盛金属７の上に直接溶接
されているが、溶接に際しては当該肉盛金属７と同様、
ＳＵＳ３４７一ＵＬＣ系の超低炭素含有量のステンレス
鋼を溶接部８に使用するものである。第１表にＳＵＳ３
４７一ＵＬＣ肉盛金属７及び溶接金属８の化学成分を示
す。このように炭素含有量がたとえば０．０３％以下の
ようにきわめて低いステンレス鋼を上記溶接部（溶接金
属）８、肉盛金属１等として使用することにより、当該
溶接部８等の脆化の主原因となるＣｒ系炭化物、あるい
はσ相の析出が少なくなるばかりでなく、炭素含有量の
低いことにともな（、Ｎｂの含有量も低くなり、したが
つてオーステナイト母相中に析出するＮｂＣ量も少なく
なり、溶接部における優れた靭性を維持することが可能
である。ちなみに、通常のＳＵＳ３４７系ステンレス鋼
の場合、Ｎｂ含有量の規格値はＣ含有量の８倍、Ｃ含有
量を０．０３％とした場合、０．２４％程度のＮｂが含
まれていると理解してよい。ステンレス鋼ＳＵＳ３４７
−ＵＬＣはＣ含有量が低イ・く、同時に上述のようにＮ
ｂ含有量も低いので、靭性の面でもきわめて優れた特質
を有し、溶接部の靭性を保持する上で有利である。A part of the internal device 4 is directly welded onto the overlay metal 7, but when welding, similar to the overlay metal 7,
SUS347-ULC stainless steel with ultra-low carbon content is used for the welding part 8. Table 1 shows SUS3
47- The chemical composition of ULC overlay metal 7 and weld metal 8 is shown. By using stainless steel with an extremely low carbon content, such as 0.03% or less, for the welding part (weld metal) 8, overlay metal 1, etc., embrittlement of the welding part 8, etc. can be prevented. Not only does the precipitation of Cr-based carbides or σ phase, which is the main cause, decrease, but also the Nb content decreases due to the low carbon content. The amount of Nb is also reduced, making it possible to maintain excellent toughness in the welded part.Incidentally, in the case of normal SUS347 stainless steel, the standard value for Nb content is 8 times the C content, and the C content is 0. If it is .03%, it can be understood that about 0.24% of Nb is included. Stainless steel SUS347
-ULC has a low C content, and at the same time, as mentioned above,
Since the b content is low, it has extremely excellent properties in terms of toughness, and is advantageous in maintaining the toughness of the weld zone.
第２表に応力除去焼鈍後の曲げ試験結果を従来溶接法と
比較して示すが、本発明になる溶接方法によれば７００
℃×５０ｈの応力除去焼鈍を行なつても割れは発生して
おらず、良好な結果が得られることが明らかである。ま
た、２イＣｒ−１Ｍ０鋼母材から、内部装置の一部にわ
たる継手の引張破断試験においては、溶接金属８で破断
したが、その強度は６０ｋ，以上であり、内部装置であ
るステンレ又鋼材材において要求されている最低強度５
３ｋｇ／一を十分に上廻つていた。以上に詳細に説明し
たように、本発明になる溶接方法は、圧力容器等の内表
面に溶接する内部装置の一部との溶接部分、あるいは当
該溶接部分と接する部分をさらに肉盛して、超低炭素の
ステンレス鋼を使用して溶接することを骨子とするもの
で、当該内部装置の取付け溶接部は溶接後の熱処理を省
略することも可能であり、したがつて熱処理に起因する
脆化を防止することが可能である。Table 2 shows the bending test results after stress relief annealing in comparison with the conventional welding method.
It is clear that no cracks were generated even when stress relief annealing was performed at 50° C. for 50 hours, and that good results were obtained. In addition, in a tensile rupture test of a joint from a 2-I Cr-1M0 steel base material to a part of the internal device, it broke at weld metal 8, but the strength was 60K or more, and the stainless steel or steel material of the internal device broke at weld metal 8. Minimum strength required for materials 5
It was well over 3kg/1. As explained in detail above, the welding method according to the present invention further includes overlaying the welded part with a part of the internal device to be welded to the inner surface of a pressure vessel or the like, or the part in contact with the welded part, The main idea is to weld using ultra-low carbon stainless steel, and it is possible to omit post-weld heat treatment for the installation welds of the internal devices, thus eliminating embrittlement caused by heat treatment. It is possible to prevent this.
またクローム系炭化物はもとより、ＮｂＣその他の炭化
物、σ相等の析出を十分に抑制することが可能となり、
したがつてこれら炭化物等の析出の母体となるδフエラ
イト母相の少なくするための調整、熱処理等も不要とな
り、またオーステナイト母相中へ主として析出するＮｂ
系炭化物ＮｂＣによつて溶接部等の靭性が害されること
も全くみられなくなつた。また溶接部の周辺に発生する
、高温加熱に起因する応力にも耐えることができ、クラ
ツクの発生、クラツクにともなう圧力容器等の水素ガス
損傷の防止にも優れた効果を呈するものであることがわ
かつた。また従来技術になる溶接方法では、溶接後の応
力除去焼鈍、あるいは溶接加熱サイクルによつて脆化が
起こることを防止し、抑制する観点から、溶接作業条件
に大きな制約がみられたが、本発明の溶接方法を適用す
ればこのような溶接施工上の大きな困難はみられず、熟
練した溶接作業者によらないでも高い熱応力に耐え、か
つ靭性に優れた溶接部を得ることが可能となつた。In addition, it is possible to sufficiently suppress the precipitation of not only chromium-based carbides but also NbC and other carbides, σ phase, etc.
Therefore, there is no need for adjustment, heat treatment, etc. to reduce the δ-ferrite matrix, which is the matrix for the precipitation of these carbides, etc., and Nb, which is mainly precipitated in the austenite matrix, becomes unnecessary.
It was also no longer observed that the toughness of welded parts etc. was impaired by the NbC carbide. It can also withstand stress caused by high-temperature heating that occurs around the weld, and is highly effective in preventing cracks and hydrogen gas damage to pressure vessels, etc., caused by cracks. I understand. In addition, in conventional welding methods, there were major restrictions on welding work conditions from the perspective of preventing and suppressing embrittlement caused by stress relief annealing after welding or welding heating cycles. If the welding method of the invention is applied, such major difficulties in welding work will not be encountered, and it will be possible to obtain welded parts that can withstand high thermal stress and have excellent toughness without requiring skilled welders. Summer.
したがつて経済的にみても、、溶接経費、省力化等の面
でも大きな効果の得られることがわかつた。Therefore, from an economic point of view, it has been found that significant effects can be obtained in terms of welding costs, labor savings, etc.
第１図及び第２図は従来技術によつて溶接した圧力容器
と肉盛金属、内部装置の一部とクラツクの発生状況を示
した斜視図及び断面図、第３図は本発明になる溶接方法
を説明するための断面図である。
１：圧力容器母材、２：肉盛金属、３：肉盛金属、４：
内部装置の一部、５：溶接金属、６：クラツク、７：肉
盛金属、８：溶接金属。Figures 1 and 2 are a perspective view and a sectional view showing a pressure vessel and overlay metal welded using the conventional technique, a part of the internal device, and the occurrence of cracks, and Figure 3 is a welding process according to the present invention. FIG. 3 is a cross-sectional view for explaining the method. 1: Pressure vessel base material, 2: Overlay metal, 3: Overlay metal, 4:
Part of internal device, 5: Weld metal, 6: Cracks, 7: Overlay metal, 8: Weld metal.
Claims (1)
、同じくステンレス鋼系素材よりなる部品を溶接する方
法において、当該ステンレス鋼系肉盛金属上にさらに別
の炭素含有量が０．０３％以下のステンレス鋼系肉盛金
属を部品溶接箇所に少なくとも一層以上肉盛溶接し、か
つ炭素含有量が０．０３％以下のステンレス鋼系肉盛金
属と、上記ステンレス鋼系素材よりなる部品との溶接接
合部に同じく炭素含有量が０．０３％以下のステンレス
鋼系溶接材を使用することを特徴とする溶接方法。1. In a method of welding a part made of a stainless steel material on a stainless steel overlay metal joined to the surface of a steel material, another carbon content of 0.03% is added to the stainless steel overlay metal. At least one layer of the following stainless steel overlay metals is overlay welded to the part welding location, and the stainless steel overlay metal with a carbon content of 0.03% or less is combined with the above stainless steel material. A welding method characterized by using a stainless steel welding material with a carbon content of 0.03% or less in the welded joint.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP5550175A JPS596743B2 (en) | 1975-05-13 | 1975-05-13 | Welding method |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP5550175A JPS596743B2 (en) | 1975-05-13 | 1975-05-13 | Welding method |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS51131436A JPS51131436A (en) | 1976-11-15 |
| JPS596743B2 true JPS596743B2 (en) | 1984-02-14 |
Family
ID=13000389
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP5550175A Expired JPS596743B2 (en) | 1975-05-13 | 1975-05-13 | Welding method |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS596743B2 (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS61137242U (en) * | 1985-02-14 | 1986-08-26 |
Families Citing this family (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS594971A (en) * | 1982-06-29 | 1984-01-11 | Kawasaki Steel Corp | Build up welding |
| JP5940311B2 (en) * | 2012-01-24 | 2016-06-29 | 三菱重工業株式会社 | Joining method and joining structure |
-
1975
- 1975-05-13 JP JP5550175A patent/JPS596743B2/en not_active Expired
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS61137242U (en) * | 1985-02-14 | 1986-08-26 |
Also Published As
| Publication number | Publication date |
|---|---|
| JPS51131436A (en) | 1976-11-15 |
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