JP3530395B2 - Welding methods, welded joints and welded structures - Google Patents
Welding methods, welded joints and welded structuresInfo
- Publication number
- JP3530395B2 JP3530395B2 JP27496998A JP27496998A JP3530395B2 JP 3530395 B2 JP3530395 B2 JP 3530395B2 JP 27496998 A JP27496998 A JP 27496998A JP 27496998 A JP27496998 A JP 27496998A JP 3530395 B2 JP3530395 B2 JP 3530395B2
- Authority
- JP
- Japan
- Prior art keywords
- welded
- stainless steel
- shaped portion
- steel base
- welding
- 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 - Lifetime
Links
- 238000003466 welding Methods 0.000 title claims description 44
- 238000000034 method Methods 0.000 title claims description 20
- 230000035515 penetration Effects 0.000 claims description 35
- 229910001220 stainless steel Inorganic materials 0.000 claims description 27
- 239000010935 stainless steel Substances 0.000 claims description 27
- 239000000463 material Substances 0.000 claims description 25
- 239000000843 powder Substances 0.000 claims description 10
- 229910044991 metal oxide Inorganic materials 0.000 claims description 9
- 150000004706 metal oxides Chemical class 0.000 claims description 9
- 239000002904 solvent Substances 0.000 claims description 9
- 238000002156 mixing Methods 0.000 claims description 7
- 239000010953 base metal Substances 0.000 claims description 6
- 239000012530 fluid Substances 0.000 claims description 6
- 239000002184 metal Substances 0.000 description 18
- 229910052751 metal Inorganic materials 0.000 description 18
- 230000001737 promoting effect Effects 0.000 description 7
- 230000000694 effects Effects 0.000 description 6
- 230000004907 flux Effects 0.000 description 5
- 239000000203 mixture Substances 0.000 description 5
- 238000005452 bending Methods 0.000 description 4
- 229910000963 austenitic stainless steel Inorganic materials 0.000 description 3
- 230000007797 corrosion Effects 0.000 description 3
- 238000005260 corrosion Methods 0.000 description 3
- 238000010586 diagram Methods 0.000 description 3
- 230000006870 function Effects 0.000 description 3
- 239000003960 organic solvent Substances 0.000 description 3
- 239000000126 substance Substances 0.000 description 3
- QAOWNCQODCNURD-UHFFFAOYSA-N Sulfuric acid Chemical compound OS(O)(=O)=O QAOWNCQODCNURD-UHFFFAOYSA-N 0.000 description 2
- 238000007545 Vickers hardness test Methods 0.000 description 2
- 239000011324 bead Substances 0.000 description 2
- 239000003795 chemical substances by application Substances 0.000 description 2
- 230000007547 defect Effects 0.000 description 2
- 102200052313 rs9282831 Human genes 0.000 description 2
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 2
- NIXOWILDQLNWCW-UHFFFAOYSA-N Acrylic acid Chemical compound OC(=O)C=C NIXOWILDQLNWCW-UHFFFAOYSA-N 0.000 description 1
- UOACKFBJUYNSLK-XRKIENNPSA-N Estradiol Cypionate Chemical compound O([C@H]1CC[C@H]2[C@H]3[C@@H](C4=CC=C(O)C=C4CC3)CC[C@@]21C)C(=O)CCC1CCCC1 UOACKFBJUYNSLK-XRKIENNPSA-N 0.000 description 1
- 101150000971 SUS3 gene Proteins 0.000 description 1
- 206010070834 Sensitisation Diseases 0.000 description 1
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 1
- 230000005540 biological transmission Effects 0.000 description 1
- 238000009835 boiling Methods 0.000 description 1
- 239000000919 ceramic Substances 0.000 description 1
- 238000000576 coating method Methods 0.000 description 1
- 238000001816 cooling Methods 0.000 description 1
- 229910000365 copper sulfate Inorganic materials 0.000 description 1
- ARUVKPQLZAKDPS-UHFFFAOYSA-L copper(II) sulfate Chemical compound [Cu+2].[O-][S+2]([O-])([O-])[O-] ARUVKPQLZAKDPS-UHFFFAOYSA-L 0.000 description 1
- 238000005336 cracking Methods 0.000 description 1
- 238000001514 detection method Methods 0.000 description 1
- 238000011156 evaluation Methods 0.000 description 1
- 238000009863 impact test Methods 0.000 description 1
- 239000007788 liquid Substances 0.000 description 1
- 229910052760 oxygen Inorganic materials 0.000 description 1
- 239000001301 oxygen Substances 0.000 description 1
- 238000011056 performance test Methods 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 230000005855 radiation Effects 0.000 description 1
- 230000008313 sensitization Effects 0.000 description 1
- 239000002002 slurry Substances 0.000 description 1
- 238000009864 tensile test Methods 0.000 description 1
Classifications
-
- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02E—REDUCTION OF GREENHOUSE GAS [GHG] EMISSIONS, RELATED TO ENERGY GENERATION, TRANSMISSION OR DISTRIBUTION
- Y02E30/00—Energy generation of nuclear origin
- Y02E30/30—Nuclear fission reactors
Landscapes
- Arc Welding In General (AREA)
- Butt Welding And Welding Of Specific Article (AREA)
- Nonmetallic Welding Materials (AREA)
Description
【０００１】[0001]
【発明の属する技術分野】本発明は、例えば原子力機器
のステンレス鋼配管継手に適用して好適な溶接方法，溶
接継手及び溶接構造物に関する。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a welding method, a welded joint and a welded structure suitable for application to, for example, a stainless steel pipe joint for nuclear equipment.
【０００２】[0002]
【従来の技術】軽水炉の一次冷却系において、ステンレ
ス鋼（オーステナイト系ステンレス鋼等）配管の取付工
事が行われるが、この際の配管継手（溶接継手）は、例
えば図１０に示すような溶接方法で施工される。2. Description of the Related Art In a primary cooling system of a light water reactor, stainless steel (austenitic stainless steel, etc.) piping is installed, and a pipe joint (welded joint) at this time is welded by a welding method as shown in FIG. Will be constructed in.
【０００３】これによれば、オーステナイト系ステンレ
ス鋼からなる管母材100 同士を、幅広のＵ型開先101 で
単に突合せ溶接をしていた。溶接法としては、TIG 溶接
を手動又は自動で行っていた。According to this, the pipe base materials 100 made of austenitic stainless steel are simply butt-welded with the wide U-shaped groove 101. As the welding method, TIG welding was performed manually or automatically.
【０００４】[0004]
【発明が解決しようとする課題】従来のオーステナイト
系ステンレス鋼の溶接部は、前述したように幅広のＵ型
開先101 で単に突合せ溶接されているため、板厚によっ
ては、多層のパス（図中では７層／７パス）により溶接
されることから、入熱量が大きく、熱影響部が鋭敏化
（炭化物の析出に伴って粒界腐食が起こりやすくなるこ
と）され易いという不具合があった。Since the conventional austenitic stainless steel welded portion is simply butt-welded with the wide U-shaped groove 101 as described above, depending on the plate thickness, a multi-layered pass (Fig. Since the welding is performed by 7 layers / 7 passes among them, there is a problem that the heat input amount is large and the heat-affected zone is easily sensitized (grain boundary corrosion easily occurs due to precipitation of carbide).
【０００５】加えて、溶接金属量増大により引張残留応
力も増大することから、前記鋭敏化と相俟って耐ＳＣＣ
（Stress Corrosion Cracking-応力腐食割れ）性が相対
的に不十分である。また、溶接工数増大によりコストア
ップも招来していた。In addition, since the tensile residual stress also increases as the amount of weld metal increases, the SCC resistance in combination with the above-mentioned sensitization is increased.
(Stress Corrosion Cracking) is relatively insufficient. In addition, an increase in welding man-hours also causes an increase in cost.
【０００６】そこで、本発明はこのような実情を踏ま
え、溶接パス数の低減による熱影響部の低鋭敏化と溶接
金属量低減による引張残留応力の低減が図れる溶接方
法，溶接継手及び溶接構造物を提供することを目的とす
る。In view of the above situation, the present invention is directed to a welding method, a welded joint and a welded structure which can reduce the heat sensitive zone by reducing the number of welding passes and the tensile residual stress by reducing the amount of weld metal. The purpose is to provide.
【０００７】[0007]
【課題を解決するための手段】前記目的を達成するため
の本発明に係る溶接方法は、ステンレス鋼母材同士を所
定の開先形状で突合せ溶接する際に、前記ステンレス鋼
母材表面に金属酸化物の粉末と溶媒を混合してなる溶込
み促進剤を塗布した後 TIG溶接することを特徴とする。
また、前記開先形状は、ステンレス鋼母材の板厚が３〜
７ｍｍの場合はＩ型に形成することを特徴とする。ま
た、前記開先形状は、ステンレス鋼母材の板厚が６ｍｍ
を越える場合は３〜７ｍｍの高さでＩ型部と該Ｉ型部か
ら所定の角度で拡がるＶ型部に形成し、残りを前記Ｖ型
部に連接して所定の幅のＵ型部に形成すると共に、前記
Ｖ型部及びＵ型部に前記溶込み促進剤を塗布することを
特徴とする。The welding method according to the present invention for attaining the above-mentioned object is such that when stainless steel base materials are butt-welded together in a predetermined groove shape, metal is applied to the surface of the stainless steel base materials. The method is characterized in that TIG welding is performed after applying a penetration accelerator formed by mixing oxide powder and a solvent.
Further, the groove shape has a plate thickness of the stainless steel base material of 3 to
For 7mm characterized that you formed in the I-type. Further, the groove shape has a plate thickness of the stainless steel base material of 6 mm.
When it exceeds the above, it is formed into an I-shaped portion with a height of 3 to 7 mm and a V-shaped portion that extends from the I-shaped portion at a predetermined angle, and the rest is connected to the V-shaped portion to form a U-shaped portion with a predetermined width. and forming, characterized that you applying said penetration accelerator in the V-shaped portion and a U-shaped section.
【０００８】前記目的を達成するための本発明に係る溶
接継手は、ステンレス鋼母材同士がその表面に金属酸化
物の粉末と溶媒を混合してなる溶込み促進剤を塗布した
状態で TIG溶接により突合せ溶接されてなることを特徴
とする。また、前記溶接継手は、原子力機器の配管継手
に適用されることを特徴とする。In order to achieve the above object, the welded joint according to the present invention is TIG welded in a state where stainless steel base materials are coated with a penetration accelerator formed by mixing a powder of a metal oxide and a solvent on their surfaces. It is characterized by being butt-welded by. Further, the welded joint is applied to a pipe joint of nuclear equipment.
【０００９】前記目的を達成するための本発明に係る溶
接構造物は、腐食性流体が接触する面を有する溶接構造
物において、溶接部における前記流体が接する側を、金
属酸化物の粉末と溶媒を混合してなる溶込み促進剤を用
いた溶込み深さの深い層としてあることを特徴とする。The welded structure according to the present invention for achieving the above object is a welded structure having a surface in contact with a corrosive fluid, wherein the side of the welded portion in contact with the fluid is a metal oxide powder and a solvent. Is used as a layer having a deep penetration depth using a penetration accelerator.
【００１０】[0010]
【発明の実施の形態】以下、本発明に係る溶接方法，溶
接継手及び溶接構造物を実施例により図面を用いて詳細
に説明する。BEST MODE FOR CARRYING OUT THE INVENTION A welding method, a welded joint and a welded structure according to the present invention will be described below in detail with reference to the accompanying drawings.
【００１１】［第１実施例］図１に示すように、所定の
板（肉）厚（約６mm）を越える例えば約８．５mmのSUS3
04やSUS316等のステンレス鋼母材（配管）１同士を突合
せ溶接する際には、先ず、図示のような基本的には狭開
先の開先２形状（寸法）が選択・加工される。[First Embodiment] As shown in FIG. 1, for example, about 8.5 mm of SUS3 that exceeds a predetermined plate (wall) thickness (about 6 mm).
When the stainless steel base materials (pipes) 1 such as 04 and SUS316 are butt-welded to each other, first, basically, a narrow groove groove 2 shape (dimension) as shown is selected and processed.
【００１２】即ち、前記開先２は、所定のルート高さ
（で示す３〜７mm）を有するＩ型部２ａと、該Ｉ型部
２ａから所定の高さ（で示す０〜２mmであるが、＋
＝３〜７mmを満たすと好適である）及び角度（で示
す６０〜１７０°）で拡がるＶ型部２ｂと、該Ｖ型部２
ｂに連接する所定の幅（で示す５〜８mm）及び高さ
（で示す全板厚（約８．５mm）−（３〜７）mm）のＵ
型部２ｃとからなる。尚、前記Ｕ型部２ｃに所定の拡が
り（で示す０〜３０°）を持たせても良い。また、全
板厚が約７mmを越えない場合は前記Ｕ型部２ｃは特に設
けなくても良い。That is, the groove 2 has an I-shaped portion 2a having a predetermined root height (3 to 7 mm shown by) and a predetermined height from the I-shaped portion 2a (0 to 2 mm shown by). , +
= 3 to 7 mm is preferable) and a V-shaped portion 2b that spreads at an angle (60 to 170 ° indicated by), and the V-shaped portion 2
U of a predetermined width (denoted by 5 to 8 mm) and height (total thickness of (8.5 mm)-(3 to 7) mm) connected to b
The mold part 2c. The U-shaped portion 2c may have a predetermined spread (0 to 30 ° indicated by). If the total plate thickness does not exceed about 7 mm, the U-shaped portion 2c need not be provided.
【００１３】次に、前記開先２のＶ型部２ｂ及びＵ型部
２ｃ（側壁部を除く）の表面に、例えば下記の表１で示
す金属酸化物の粉末と有機溶媒を混合してなるスラリー
状の溶込み促進剤（複組成フラックス）３を、数百μｍ
程度の厚さで、刷毛塗りする。Next, the surfaces of the V-shaped portion 2b and the U-shaped portion 2c (excluding the side wall portion) of the groove 2 are formed by mixing, for example, a metal oxide powder shown in Table 1 below and an organic solvent. Slurry of penetration accelerator (complex composition flux) 3 of several hundred μm
Brush with a certain thickness.
【００１４】[0014]
【表１】 [Table 1]
【００１５】そして、前記有機溶媒が揮発して乾燥した
後、例えば下記の表２で示す溶接要領で、通常の TIG溶
接を行う。Then, after the organic solvent is volatilized and dried, normal TIG welding is performed, for example, in the welding procedure shown in Table 2 below.
【００１６】[0016]
【表２】 [Table 2]
【００１７】この際、図２に示すように、Ｖ型部２ｂ及
びＵ型部２ｃの表面に塗布した溶込み促進剤３の溶込み
促進機能により、Ｉ型部２ａとＶ型部２ｂが１層／１パ
スで溶接される。しかも、この時の溶接金属４ａは幅が
狭く深い溶込み形状を呈する（図２の（ａ）参照）。そ
して、残りのＵ型部２ｃは２層／２パスで溶接される
（図２の（ｂ）の溶接金属４ｂ及び図２の（ｃ）の溶接
金属４ｃ参照）。At this time, as shown in FIG. 2, the I-shaped portion 2a and the V-shaped portion 2b are brought to 1 by the penetration promoting function of the penetration accelerator 3 applied to the surfaces of the V-shaped portion 2b and the U-shaped portion 2c. Welded in 1 layer / pass. Moreover, at this time, the weld metal 4a has a narrow width and a deep penetration shape (see FIG. 2A). Then, the remaining U-shaped portion 2c is welded in two layers / 2 passes (see the weld metal 4b of FIG. 2B and the weld metal 4c of FIG. 2C).
【００１８】試験（図３に示す溶込み促進フラックス試
験結果参照）により、前記１層目の溶込みは溶込み促進
剤３を塗布しない従来の TIG溶接法の約３倍の深さとな
ることを確認しているが、これは、前記溶込み促進剤３
が TIGアークを開先２中に絞る効果があるため、溶融池
の対流が中央に流れ込む形となり、これがためにビード
（溶接金属４ａ）幅が狭くなり溶込みが大きくなるので
ある。According to a test (see the result of the penetration promoting flux test shown in FIG. 3), the penetration of the first layer is about three times as deep as the conventional TIG welding method in which the penetration promoting agent 3 is not applied. It has been confirmed that this is the penetration accelerator 3
Has the effect of narrowing the TIG arc into the groove 2, so that convection in the molten pool flows into the center, which narrows the width of the bead (welding metal 4a) and increases the penetration.
【００１９】また、前記図３に示す試験結果は、板
（肉）厚が３２mmのビードオンプレート溶接におけるも
のであるが、これからは、溶込み促進剤３を何度ぬって
もビード幅と溶込み深さはさほど変わらないことと、ア
ロンセラミックＤ（商品名）を塗布した場合にも同様の
効果が得られることが判る。尚、溶込み促進剤３の溶込
み促進機能については、ビードオンプレート溶接ではあ
るが、1997年4 月発行のWELDING JOURNAL 57〜62頁，特
開昭52-39544号公報等で既に知られている。The test results shown in FIG. 3 are for bead-on-plate welding with a plate (wall) thickness of 32 mm. It can be seen that the embedding depth does not change so much and that the same effect can be obtained when Aron Ceramic D (trade name) is applied. Regarding the penetration promoting function of penetration accelerator 3, it is already known in WELDING JOURNAL, pages 57 to 62, Japanese Patent Laid-Open No. 52-39544, issued in April 1997, though it is bead-on-plate welding. There is.
【００２０】このように溶接パス数が低減されることに
より、上記表２からも判るように、入熱量の低減による
熱影響部の低鋭敏化と溶接金属量低減による引張残留応
力の低減が図れ、耐ＳＣＣ性が著しく向上する。勿論、
溶接パス数の低減により、溶接工数が削減され、コスト
ダウンが図れる。これらの結果、溶存酸素を含む高温高
圧水等の腐食性雰囲気下にさらされる配管継手に適用す
ると好適である。By reducing the number of welding passes in this way, as can be seen from Table 2 above, the heat-affected zone can be made less sensitive by reducing the amount of heat input and the tensile residual stress can be reduced by reducing the amount of weld metal. , SCC resistance is significantly improved. Of course,
By reducing the number of welding passes, the welding man-hours are reduced, and the cost can be reduced. As a result of these, it is suitable to be applied to a pipe joint exposed to a corrosive atmosphere such as high temperature and high pressure water containing dissolved oxygen.
【００２１】［第２実施例］図４に示すように、板
（肉）厚が約６mmの下記の表３に示すような化学成分の
ステンレス鋼母材（配管）１０同士を突合せ溶接する際
には、先ず、Ｉ型開先１１が選択・加工される。[Second Embodiment] As shown in FIG. 4, when butt-welding stainless steel base materials (pipes) 10 having a chemical composition as shown in Table 3 below having a plate (wall) thickness of about 6 mm, First, the I-shaped groove 11 is selected and processed.
【００２２】[0022]
【表３】 [Table 3]
【００２３】次に、前記ステンレス鋼母材（配管）１０
の表面に、第１実施例と同一の溶込み促進剤３を、図５
に示すフラックス塗布方法中、例えばNo.１〜No.３の塗
布方法を参照して刷毛塗りする。Next, the stainless steel base material (pipe) 10
The same penetration accelerator 3 as that of the first embodiment is applied to the surface of
In the flux application method shown in (1), for example, brush application is performed by referring to No. 1 to No. 3 application methods.
【００２４】そして、第１実施例と同様に、有機溶媒が
揮発して乾燥した後、例えば下記の表４で示す溶接要領
で、通常の TIG溶接を行う。Then, as in the first embodiment, after the organic solvent is volatilized and dried, normal TIG welding is performed, for example, in the welding procedure shown in Table 4 below.
【００２５】[0025]
【表４】 [Table 4]
【００２６】この際、図５のNo.１〜No.３の塗布方法か
らも判るように、ステンレス鋼母材（配管）１０の表面
に塗布した溶込み促進剤３の溶込み促進機能により、前
記Ｉ型開先１１が１層／１パスで溶接される。しかも、
この時の溶接金属４の幅も狭い。At this time, as can be seen from the coating methods No. 1 to No. 3 in FIG. 5, the penetration promoting function of the penetration promoting agent 3 applied to the surface of the stainless steel base material (pipe) 10 The I-shaped groove 11 is welded in one layer / one pass. Moreover,
The width of the weld metal 4 at this time is also narrow.
【００２７】次に、このように溶接された溶接継手の性
能試験評価結果を下記の表５乃至表７と図６乃至図８に
基づいて説明する。Next, performance test evaluation results of the welded joint thus welded will be described based on the following Tables 5 to 7 and FIGS. 6 to 8.
【００２８】[0028]
【表５】 [Table 5]
【００２９】[0029]
【表６】 [Table 6]
【００３０】[0030]
【表７】 [Table 7]
【００３１】上記表５は、溶接金属部と母材の化学成分
比較を示すもので、この成分分析結果から、母材及び溶
接金属部の化学成分に有意差は認められなかった。Table 5 above shows a comparison of the chemical components of the weld metal and the base metal. From the results of this component analysis, no significant difference was observed in the chemical components of the base metal and the weld metal.
【００３２】また、図６は、溶接金属部のマクロ組織写
真及び溶接金属部・境界部（ＨＡＺ部）・母材のミクロ
組織写真を示すもので、これらから判るように、割れ等
の溶接欠陥はなく、良好であった。FIG. 6 shows a photograph of the macrostructure of the weld metal portion and a photograph of the microstructure of the weld metal portion / boundary portion (HAZ portion) / base metal. As can be seen from these, welding defects such as cracks are shown. Not good.
【００３３】上記表６は、継手引張試験結果を示すもの
で、室温（RT）での引張強度はmin.633N/mm2，また高温
（３６０°）での引張強度はmin.457N/mm2であり、それ
ぞれ告示501 号に規定されている最小引張強さを満足し
ており、良好であった。Table 6 above shows the results of the joint tensile test. The tensile strength at room temperature (RT) was min. 633 N / mm 2 , and the tensile strength at high temperature (360 °) was min. 457 N / mm 2. Each of them satisfied the minimum tensile strength specified in Notification No. 501 and was good.
【００３４】また、図７は、ビッカース硬さ試験結果を
示すもので、溶接金属部（Depo) の硬さはHv＝174 〜 1
88であり、従来 TIG溶接法による溶金部の硬さHv＝170
〜 210と同等であり、良好であった。FIG. 7 shows the results of the Vickers hardness test. The hardness of the weld metal part (Depo) is Hv = 174-1.
88, which is the hardness of the molten metal by the conventional TIG welding method Hv = 170
It was equivalent to ~ 210 and was good.
【００３５】上記表７は、溶接金属部・ＨＡＺ部及び母
材のシャルピー衝撃試験結果を示すもので、吸収エネル
ギ等靭性の低下はなく、良好であった。Table 7 above shows the results of the Charpy impact test of the weld metal part / HAZ part and the base metal, which were good without a decrease in toughness such as absorbed energy.
【００３６】また、図８は、表曲げ，裏曲げ試験の結果
を示すもので、全ての試験片において割れ等はなく、良
好であった。FIG. 8 shows the results of the front bending test and the back bending test. All the test pieces were good with no cracks or the like.
【００３７】また、この他に、沸騰硫酸・硫酸銅溶液中
に入れて腐食試験後、曲げ試験を行った結果、割れはな
く良好であった。更に、放射線透過試験及び液体浸透探
傷試験を行った結果、欠陥の指示はなく、良好であっ
た。In addition, as a result of conducting a bending test after the corrosion test by putting the solution in a boiling sulfuric acid / copper sulfate solution, it was found to be good with no cracks. Furthermore, as a result of the radiation transmission test and the liquid penetrant flaw detection test, there was no indication of defects, and it was good.
【００３８】また、図９は、各種単組成溶込み促進剤に
よる深溶込み溶接試験結果（母材SUS304，板厚６mm）を
示すものである。これらによっても、ビード幅の狭い１
パス貫通溶接が可能となる。FIG. 9 shows the results of deep penetration welding tests (base material SUS304, plate thickness 6 mm) using various single-composition penetration accelerators. With these, the bead width is narrow 1
Pass-through welding is possible.
【００３９】尚、本発明は上記各実施例に限定されず、
本発明の要旨を逸脱しない範囲で、各種変更が可能であ
ることはいうまでもない。The present invention is not limited to the above embodiments,
It goes without saying that various changes can be made without departing from the scope of the present invention.
【００４０】[0040]
【発明の効果】請求項１の発明によれば、ステンレス鋼
母材同士を所定の開先形状で突合せ溶接する際に、前記
ステンレス鋼母材表面に金属酸化物の粉末と溶媒を混合
してなる溶込み促進剤を塗布した後 TIG溶接することを
特徴とするので、溶接パス数が低減され、入熱量の低減
による熱影響部の低鋭敏化と溶接金属量低減による引張
残留応力の低減が図れ、耐ＳＣＣ性が著しく向上する。
勿論、溶接パス数の低減により、溶接工数が削減され、
コストダウンが図れる。According to the invention of claim 1, when the stainless steel base materials are butt-welded together in a predetermined groove shape, a metal oxide powder and a solvent are mixed on the surface of the stainless steel base materials. Since it is characterized by TIG welding after applying a penetration accelerator, the number of welding passes is reduced, the heat-affected zone is made less sensitive by reducing the heat input, and the tensile residual stress is reduced by reducing the amount of weld metal. The SCC resistance is remarkably improved.
Of course, by reducing the number of welding passes, the welding man-hours are reduced,
The cost can be reduced.
【００４１】請求項２の発明によれば、前記開先形状
は、ステンレス鋼母材の板厚が３〜７ｍｍの場合はＩ型
に形成することを特徴とするので、１パスの全溶込み溶
接が可能となり、請求項１の発明と同様の効果が得られ
る。[0041] According to the invention of claim 2, wherein the groove shape, since the thickness of the stainless steel base metal in the case of 3~7mm characterized that you formed in the I-type, completely dissolved in 1 pass It becomes possible to carry out penetration welding, and the same effect as the invention of claim 1 can be obtained.
【００４２】請求項３の発明によれば、前記開先形状
は、ステンレス鋼母材の板厚が６ｍｍを越える場合は３
〜７ｍｍの高さでＩ型部と該Ｉ型部から所定の角度で拡
がるＶ型部に形成し、残りを前記Ｖ型部に連接して所定
の幅のＵ型部に形成すると共に、前記Ｖ型部及びＵ型部
に前記溶込み促進剤を塗布することを特徴とするので、
請求項１の発明と同様の効果が得られる。According to the invention of claim 3, the groove shape is 3 when the plate thickness of the stainless steel base material exceeds 6 mm.
Forming a I-shaped portion at a height of ˜7 mm and a V-shaped portion that extends from the I-shaped portion at a predetermined angle, and connecting the rest to the V-shaped portion to form a U-shaped portion having a predetermined width. because characterized that you applying said penetration accelerator in V-shaped portion and a U-shaped section,
The same effect as the invention of claim 1 can be obtained.
【００４３】請求項４の発明によれば、ステンレス鋼母
材同士がその表面に金属酸化物の粉末と溶媒を混合して
なる溶込み促進剤を塗布した状態で TIG溶接により突合
せ溶接されてなることを特徴とするので、請求項１の発
明と同様の効果が得られ、溶接継手の信頼性が高まる。According to the fourth aspect of the present invention, the stainless steel base materials are butt-welded by TIG welding in a state in which the penetration accelerator formed by mixing the powder of the metal oxide and the solvent is applied to the surfaces of the stainless steel base materials. Therefore, the same effect as that of the invention of claim 1 is obtained, and the reliability of the welded joint is enhanced.
【００４４】請求項５の発明によれば、前記溶接継手
は、原子力機器の配管継手に適用されることを特徴とす
るので、原子力機器において信頼性の高い配管継手が実
現される。According to the invention of claim 5, the welded joint is applied to a pipe joint of a nuclear power equipment, so that a highly reliable pipe joint is realized in a nuclear power equipment.
【００４５】請求項６の発明によれば、腐食性流体が接
触する面を有する溶接構造物において、溶接部における
前記流体が接する側を、金属酸化物の粉末と溶媒を混合
してなる溶込み促進剤を用いた溶込み深さの深い層とし
てあることを特徴とするので、請求項１の発明と同様の
効果が得られ、信頼性の高い溶接構造物が実現される。According to the sixth aspect of the present invention, in a welded structure having a surface in contact with a corrosive fluid, the side of the welded portion in contact with the fluid is a mixture of a metal oxide powder and a solvent. Since it is characterized by being a layer having a deep penetration depth using an accelerator, the same effect as the invention of claim 1 can be obtained, and a highly reliable welded structure can be realized.
【図１】本発明の第１実施例を示すステンレス鋼母材の
説明図である。FIG. 1 is an explanatory diagram of a stainless steel base material showing a first embodiment of the present invention.
【図２】同じく TIG溶接の工程図である。FIG. 2 is a process drawing of TIG welding.
【図３】同じく溶込み促進フラックス試験結果の説明図
である。FIG. 3 is an explanatory view of the results of a penetration promoting flux test.
【図４】本発明の第２実施例を示すステンレス鋼母材の
説明図である。FIG. 4 is an explanatory view of a stainless steel base material showing a second embodiment of the present invention.
【図５】同じくフラックス塗布方法の影響の説明図であ
る。FIG. 5 is an explanatory view of the influence of the flux applying method.
【図６】同じくマクロ・ミクロ組織写真である。FIG. 6 is also a macro / micro structure photograph.
【図７】同じくビッカース硬さ試験結果の説明図であ
る。FIG. 7 is an explanatory view of Vickers hardness test results.
【図８】同じく曲げ試験結果の説明図である。FIG. 8 is an explanatory diagram of a bending test result similarly.
【図９】同じく各種単組成溶込み促進剤による深溶込み
溶接試験結果の説明図である。FIG. 9 is an explanatory view of the results of deep penetration welding test using various single-composition penetration accelerators.
【図１０】従来の TIG溶接法の説明図である。FIG. 10 is an explanatory diagram of a conventional TIG welding method.
１ ステンレス鋼母材（配管） ２ 開先 ２ａ Ｉ型部 ２ｂ Ｖ型部 ２ｃ Ｕ型部 ３ 溶込み促進剤 ４，４ａ，４ｂ，４ｃ 溶接金属 １０ ステンレス鋼母材（配管） １１ Ｉ型開先 1 Stainless steel base material (piping) 2 bevel 2a I type part 2b V type part 2c U type part 3 Penetration accelerator 4,4a, 4b, 4c Weld metal 10 Stainless steel base material (piping) 11 Type I groove
フロントページの続き (51)Int.Cl.7 識別記号 ＦＩ Ｂ２３Ｋ 35/362 Ｂ２３Ｋ 35/362 Ａ Ｇ２１Ｃ 19/02 Ｇ２１Ｃ 19/02 Ｊ (72)発明者 松島 健 兵庫県神戸市兵庫区和田崎町一丁目１番 １号 三菱重工業株式会社 神戸造船所 内 (72)発明者 佐藤 力哉 兵庫県神戸市兵庫区和田崎町一丁目１番 １号 三菱重工業株式会社 神戸造船所 内 (56)参考文献 特開2000−71094（ＪＰ，Ａ) 特開 平３−258463（ＪＰ，Ａ) 特開 平６−320277（ＪＰ，Ａ) 特開 平３−52775（ＪＰ，Ａ) 特公 昭44−127（ＪＰ，Ｂ１) (58)調査した分野(Int.Cl.7，ＤＢ名) B23K 9/028 B23K 9/167 B23K 9/23 B23K 33/00 Front page continuation (51) Int.Cl. 7 Identification code FI B23K 35/362 B23K 35/362 A G21C 19/02 G21C 19/02 J (72) Inventor Ken Matsushima Ken Wadazaki-cho, Hyogo-ku, Hyogo-ken 1-1-1 Mitsubishi Heavy Industries, Ltd. Kobe Shipyard (72) Inventor Rikiya Sato 1-1-1 Wadasaki-cho, Hyogo-ku, Kobe-shi, Hyogo Mitsubishi Heavy Industries Ltd. Kobe Shipyard (56) References Special Open 2000-71094 (JP, A) JP-A-3-258463 (JP, A) JP-A-6-320277 (JP, A) JP-A-3-52775 (JP, A) JP-B-44-127 (JP , B1) (58) Fields investigated (Int.Cl. 7 , DB name) B23K 9/028 B23K 9/167 B23K 9/23 B23K 33/00
Claims (6)
で突合せ溶接する際に、前記ステンレス鋼母材表面に金
属酸化物の粉末と溶媒を混合してなる溶込み促進剤を塗
布した後 TIG溶接することを特徴とする溶接方法。1. When butt-welding stainless steel base materials in a predetermined groove shape, after applying a penetration accelerator formed by mixing a metal oxide powder and a solvent on the surface of the stainless steel base materials Welding method characterized by TIG welding.
厚が３〜７ｍｍの場合はＩ型に形成することを特徴とす
る請求項１に記載の溶接方法。Wherein said groove shape, welding method of claim 1 the plate thickness of the stainless steel base metal in the case of 3~7mm characterized that you formed in the I-type.
厚が６ｍｍを越える場合は３〜７ｍｍの高さでＩ型部と
該Ｉ型部から所定の角度で拡がるＶ型部に形成し、残り
を前記Ｖ型部に連接して所定の幅のＵ型部に形成すると
共に、前記Ｖ型部及びＵ型部に前記溶込み促進剤を塗布
することを特徴とする請求項１に記載の溶接方法。Wherein the groove shape is formed in a V-shaped portion extending at a predetermined angle from the I-shaped portion and the I-type section at the height of 3~7mm If the thickness of the stainless steel base material exceeds 6mm And the rest
The continuously connected to the V-shaped portion formed on the U-shaped portion of predetermined width Then
Both of the V-shaped portion and the U-shaped portion are coated with the penetration accelerator.
Welding method according to claim 1, wherein to Rukoto.
酸化物の粉末と溶媒を混合してなる溶込み促進剤を塗布
した状態で TIG溶接により突合せ溶接されてなることを
特徴とする溶接継手。4. A welded joint characterized in that stainless steel base materials are butt-welded by TIG welding in a state in which a penetration accelerator formed by mixing a powder of a metal oxide and a solvent is applied to the surfaces of the stainless steel base materials. .
に適用されることを特徴とする請求項４に記載の溶接継
手。5. The welded joint according to claim 4, wherein the welded joint is applied to a pipe joint of nuclear equipment.
造物において、溶接部における前記流体が接する側を、
金属酸化物の粉末と溶媒を混合してなる溶込み促進剤を
用いた溶込み深さの深い層としてあることを特徴とする
溶接構造物。6. A welded structure having a surface in contact with a corrosive fluid, wherein a side of the welded portion in contact with the fluid is
A welded structure having a deep penetration depth using a penetration accelerator formed by mixing a powder of a metal oxide and a solvent.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP27496998A JP3530395B2 (en) | 1998-09-29 | 1998-09-29 | Welding methods, welded joints and welded structures |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP27496998A JP3530395B2 (en) | 1998-09-29 | 1998-09-29 | Welding methods, welded joints and welded structures |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JP2000102890A JP2000102890A (en) | 2000-04-11 |
| JP3530395B2 true JP3530395B2 (en) | 2004-05-24 |
Family
ID=17549098
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP27496998A Expired - Lifetime JP3530395B2 (en) | 1998-09-29 | 1998-09-29 | Welding methods, welded joints and welded structures |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP3530395B2 (en) |
Families Citing this family (9)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| RU2262425C1 (en) * | 2004-02-06 | 2005-10-20 | Открытое акционерное общество "Комсомольское-на-Амуре авиационное производственное объединение им. Ю.А. Гагарина" | Titanium alloy electric arc welding method |
| JP5594813B2 (en) * | 2009-06-12 | 2014-09-24 | 愛知産業株式会社 | Narrow groove welding method for thick steel plates and steel pipes |
| JP5594814B2 (en) * | 2009-06-12 | 2014-09-24 | 愛知産業株式会社 | Tube welding method to circumferentially curved surface |
| EP2787167B1 (en) | 2013-04-04 | 2018-12-26 | Ansaldo Energia IP UK Limited | Method for welding rotors for power generation |
| CN110144540B (en) * | 2019-06-13 | 2021-06-22 | 深圳大学 | Tungsten composite coating on first wall of cladding and preparation method thereof |
| US20210178526A1 (en) * | 2019-12-12 | 2021-06-17 | National Pingtung University Of Science & Technology | TIG Welding Flux for Super Duplex Stainless Steel |
| CN112404727A (en) * | 2020-10-27 | 2021-02-26 | 中国核动力研究设计院 | Square tube assembling and welding method and welding protection device |
| RU2757447C1 (en) * | 2020-12-21 | 2021-10-15 | Дмитрий Борисович Фрункин | Method for welding large diameter straight-seam pipes |
| CN120002125B (en) * | 2023-11-15 | 2026-03-17 | 宝山钢铁股份有限公司 | Methods for optimizing the microstructure and toughness of welded joints in stainless steel composite plates and their welded components |
-
1998
- 1998-09-29 JP JP27496998A patent/JP3530395B2/en not_active Expired - Lifetime
Also Published As
| Publication number | Publication date |
|---|---|
| JP2000102890A (en) | 2000-04-11 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| KR101291022B1 (en) | Material composite with explosion-welded intermediate piece | |
| JP3530395B2 (en) | Welding methods, welded joints and welded structures | |
| Sabry et al. | Flange joining using friction stir welding and tungsten inert gas welding of AA6082: a comparison based on joint performance | |
| Küçüköner et al. | Investigation of microstructure and mechanical properties of AISI2205/DIN-P355GH steel joint by submerged arc welding | |
| CN114273764B (en) | Butt joint girth weld welding method for high-strength steel plate steel pipe piles | |
| Porchilamban et al. | Structural relationships of metallurgical and mechanical properties influenced by Ni-based fillers on Gas Tungsten Arc Welded Ferritic/Austenitic SS dissimilar joints | |
| El-Batahgy | Laser beam welding of austenitic stainless steels–Similar butt and dissimilar lap joints | |
| de Bribean Guerra et al. | Air carbon arc gouging and submerged-arc welding: Insights into sensitization and mechanical behavior of AISI 2205 duplex stainless steel | |
| Madhankumar et al. | Optimization of ultimate tensile strength of welded Inconel 625 and duplex 2205 | |
| Abdulsalam | Mechanical Properties of welded steel pipes type 213 Gr T5 used in heat exchangers | |
| JP2002219585A (en) | Structures and repair methods | |
| Woods | Quality and inspection | |
| Akonyi et al. | Optimisation of process parameters for MAG welding of API X70m material to predict tensile strength using Taguchi method | |
| SU712210A1 (en) | Method of arc welding of stainless steels of the austenite class | |
| Gooch et al. | Review of Welding Practice for Carbon Steel Deaerator Vessels | |
| Nguyen et al. | WPS Design of Dissimilar Metal Welds between Austenitic Stainless Steel and Carbon Steel for Building Thermal Power Plants | |
| Mróz et al. | Study of the TIG Welding Process of Thin-Walled Components Made of 17-4 PH Steel in the Aspect of Weld Distortion Distribution. Materials 2023, 16, 4854 | |
| JP3007243B2 (en) | Prevention method of bend at the bevel on the diagonal side of the bevel of the Uranami bead in multi-groove groove welding | |
| Akume | Fundamentals of Weld Repair | |
| JPS6030585A (en) | Production of stainless clad steel pipe | |
| Hadzihafizovic | Welding Inspector-Questions & Answers | |
| Cabural et al. | Assessment of Mechanical Strength of A36 Steel with Flux Cored Arc Welding Process | |
| Oladele et al. | DISCOVERY | |
| Uemoto et al. | Welded Joint Evaluation for Chromium Controlled Carbon Steel Piping to Improve FAC Resistance | |
| Abdulsalam | Mechanical Properties of Weld Joint aluminum to copper pipes in refrigeration system |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| A521 | Written amendment |
Free format text: JAPANESE INTERMEDIATE CODE: A523 Effective date: 20040114 |
|
| TRDD | Decision of grant or rejection written | ||
| A01 | Written decision to grant a patent or to grant a registration (utility model) |
Free format text: JAPANESE INTERMEDIATE CODE: A01 Effective date: 20040210 |
|
| A61 | First payment of annual fees (during grant procedure) |
Free format text: JAPANESE INTERMEDIATE CODE: A61 Effective date: 20040227 |
|
| FPAY | Renewal fee payment (event date is renewal date of database) |
Free format text: PAYMENT UNTIL: 20080305 Year of fee payment: 4 |
|
| FPAY | Renewal fee payment (event date is renewal date of database) |
Free format text: PAYMENT UNTIL: 20090305 Year of fee payment: 5 |
|
| FPAY | Renewal fee payment (event date is renewal date of database) |
Free format text: PAYMENT UNTIL: 20100305 Year of fee payment: 6 |
|
| FPAY | Renewal fee payment (event date is renewal date of database) |
Free format text: PAYMENT UNTIL: 20110305 Year of fee payment: 7 |
|
| FPAY | Renewal fee payment (event date is renewal date of database) |
Free format text: PAYMENT UNTIL: 20110305 Year of fee payment: 7 |
|
| FPAY | Renewal fee payment (event date is renewal date of database) |
Free format text: PAYMENT UNTIL: 20120305 Year of fee payment: 8 |
|
| FPAY | Renewal fee payment (event date is renewal date of database) |
Free format text: PAYMENT UNTIL: 20130305 Year of fee payment: 9 |
|
| FPAY | Renewal fee payment (event date is renewal date of database) |
Free format text: PAYMENT UNTIL: 20140305 Year of fee payment: 10 |
|
| EXPY | Cancellation because of completion of term |