JPH03258490A - Submerged arc welding of cr-mo low alloy steel - Google Patents
Submerged arc welding of cr-mo low alloy steelInfo
- Publication number
- JPH03258490A JPH03258490A JP5777090A JP5777090A JPH03258490A JP H03258490 A JPH03258490 A JP H03258490A JP 5777090 A JP5777090 A JP 5777090A JP 5777090 A JP5777090 A JP 5777090A JP H03258490 A JPH03258490 A JP H03258490A
- Authority
- JP
- Japan
- Prior art keywords
- flux
- wire
- low alloy
- submerged arc
- arc 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.)
- Pending
Links
- 238000003466 welding Methods 0.000 title claims abstract description 31
- 229910000851 Alloy steel Inorganic materials 0.000 title claims description 13
- 230000004907 flux Effects 0.000 claims abstract description 38
- 229910052751 metal Inorganic materials 0.000 claims abstract description 36
- 239000002184 metal Substances 0.000 claims abstract description 36
- 238000000034 method Methods 0.000 claims abstract description 13
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 9
- 229910052720 vanadium Inorganic materials 0.000 claims abstract description 9
- 229910052715 tantalum Inorganic materials 0.000 claims abstract description 8
- BVKZGUZCCUSVTD-UHFFFAOYSA-L Carbonate Chemical compound [O-]C([O-])=O BVKZGUZCCUSVTD-UHFFFAOYSA-L 0.000 claims abstract description 5
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 4
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 4
- 229910052739 hydrogen Inorganic materials 0.000 abstract description 19
- 239000001257 hydrogen Substances 0.000 abstract description 18
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 abstract description 17
- 229910000831 Steel Inorganic materials 0.000 abstract description 9
- 239000010959 steel Substances 0.000 abstract description 9
- WUKWITHWXAAZEY-UHFFFAOYSA-L calcium difluoride Chemical compound [F-].[F-].[Ca+2] WUKWITHWXAAZEY-UHFFFAOYSA-L 0.000 abstract description 2
- 229910001634 calcium fluoride Inorganic materials 0.000 abstract description 2
- 230000006872 improvement Effects 0.000 abstract description 2
- 239000000956 alloy Substances 0.000 abstract 2
- 229910045601 alloy Inorganic materials 0.000 abstract 2
- 230000007423 decrease Effects 0.000 description 15
- 239000001301 oxygen Substances 0.000 description 14
- 229910052760 oxygen Inorganic materials 0.000 description 14
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 13
- 230000007774 longterm Effects 0.000 description 7
- 230000000694 effects Effects 0.000 description 6
- 238000000137 annealing Methods 0.000 description 3
- 239000011324 bead Substances 0.000 description 3
- 230000008859 change Effects 0.000 description 3
- 238000001816 cooling Methods 0.000 description 3
- 238000005336 cracking Methods 0.000 description 3
- 238000009863 impact test Methods 0.000 description 3
- 150000004649 carbonic acid derivatives Chemical class 0.000 description 2
- 239000013256 coordination polymer Substances 0.000 description 2
- 239000007789 gas Substances 0.000 description 2
- 150000002739 metals Chemical class 0.000 description 2
- 230000003647 oxidation Effects 0.000 description 2
- 238000007254 oxidation reaction Methods 0.000 description 2
- 239000000843 powder Substances 0.000 description 2
- 229910001149 41xx steel Inorganic materials 0.000 description 1
- 229910014458 Ca-Si Inorganic materials 0.000 description 1
- 229910002551 Fe-Mn Inorganic materials 0.000 description 1
- 229910004688 Ti-V Inorganic materials 0.000 description 1
- 229910010968 Ti—V Inorganic materials 0.000 description 1
- 239000010953 base metal Substances 0.000 description 1
- 229910002091 carbon monoxide Inorganic materials 0.000 description 1
- 239000003795 chemical substances by application Substances 0.000 description 1
- 239000003245 coal Substances 0.000 description 1
- 230000000052 comparative effect Effects 0.000 description 1
- 238000007796 conventional method Methods 0.000 description 1
- 229910052802 copper Inorganic materials 0.000 description 1
- 230000002950 deficient Effects 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- 238000010438 heat treatment Methods 0.000 description 1
- 150000002431 hydrogen Chemical class 0.000 description 1
- 238000004519 manufacturing process Methods 0.000 description 1
- 239000000463 material Substances 0.000 description 1
- 239000000203 mixture Substances 0.000 description 1
- 229910052758 niobium Inorganic materials 0.000 description 1
- 150000002926 oxygen Chemical class 0.000 description 1
- 230000008569 process Effects 0.000 description 1
- 230000009467 reduction Effects 0.000 description 1
- 210000000323 shoulder joint Anatomy 0.000 description 1
- 229910052709 silver Inorganic materials 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
- 238000005496 tempering Methods 0.000 description 1
- 238000009864 tensile test Methods 0.000 description 1
- 229910052718 tin Inorganic materials 0.000 description 1
- 235000013619 trace mineral Nutrition 0.000 description 1
- 239000011573 trace mineral Substances 0.000 description 1
Landscapes
- Arc Welding In General (AREA)
- Nonmetallic Welding Materials (AREA)
Abstract
Description
【発明の詳細な説明】
（産業上の利用分野）
本発明はＣｒ−Ｍｏ系低合金鋼のサブマージアーク溶接
方法に関し、詳しくは短時間から長時間の応力除去焼鈍
（以下ＳＲという）を行なった後も高温で高いクリープ
破断強度が得られ、かつ高い靭性を有するとともに、構
造物が高温で長時間使用される場合に起こる脆化（以下
使用中脆化という）、さらに水素雰囲気で使用される場
合に起こる水素脆化の程度が極めて少ない溶接金属部を
得るためのサブマージアーク溶接方法に関するものであ
る。[Detailed Description of the Invention] (Industrial Application Field) The present invention relates to a submerged arc welding method for Cr-Mo based low alloy steel, and more specifically, stress relief annealing (hereinafter referred to as SR) is performed for a short time to a long time. In addition to achieving high creep rupture strength at high temperatures and high toughness, it also prevents embrittlement that occurs when structures are used at high temperatures for long periods of time (hereinafter referred to as embrittlement during use), and when used in a hydrogen atmosphere. The present invention relates to a submerged arc welding method for obtaining a weld metal part in which the degree of hydrogen embrittlement that occurs is extremely small.
（従来の技術）
ここにいうＣｒ−Ｍｏ系低合金鋼とは、石油化学工業等
に用いられる中高温圧力容器用鋼材を意味するもので、
具体的には２１．／４Ｃｒ −Ｉ Ｍｏ鋼あるいは３Ｃ
ｒ−ＩＭｏ鋼等のことである。(Prior art) The Cr-Mo based low alloy steel referred to here means a steel material for medium and high temperature pressure vessels used in the petrochemical industry, etc.
Specifically, 21. /4Cr-I Mo steel or 3C
This refers to r-IMo steel, etc.
近年の溶接構造物の大型化や使用条件の苛酷化、さらに
は石油の代替エネルギーとして注目されている石炭液化
装置では、高温高圧操業となるため、使用鋼板が極厚化
し、その上高強度化、高クリープ破断強度化の方向にあ
る。In recent years, welded structures have become larger and the operating conditions have become more severe, and coal liquefaction equipment, which is attracting attention as an energy alternative to oil, operates at high temperatures and high pressures, so the steel plates used are extremely thick and high-strength. , the trend is towards higher creep rupture strength.
そのため、溶接金属に対しても高強度で、高クリープ破
断強度が得られ、かつ高い靭性を有するとともに、使用
中脆化および水素脆化の極めて少ないものであることが
要求され、その要求値は益々厳しくなってきている。Therefore, the weld metal is required to have high strength, high creep rupture strength, high toughness, and extremely low embrittlement and hydrogen embrittlement during use, and the required values are It's getting more and more difficult.
これら溶接金属の強度、クリープ破断強度、靭性、使用
中脆化特性および水素脆化特性に影響する大きな要因と
してＳＲ条件がある。SR conditions are a major factor that influences the strength, creep rupture strength, toughness, in-use embrittlement characteristics, and hydrogen embrittlement characteristics of these weld metals.
即ち、ＳＲは溶接によって生じた溶接部の残留応力を除
去するとともに、溶接部の靭性を向上するものであるが
、短時間であると靭性が向上せず、また強度が高すぎる
ため、水素脆化特性が確保できず、かといって長時間に
亘ると、強度およびクリープ破断強度の低下をきたす問
題がある。In other words, SR removes the residual stress in the weld caused by welding and improves the toughness of the weld, but if it is used for a short time, the toughness does not improve and the strength is too high, causing hydrogen embrittlement. However, if it continues for a long time, the strength and creep rupture strength will decrease.
板厚１００ｍｍを超える極厚のＣｒ−Ｍｏ系低合金鋼の
場合は、−船釣に９８０℃±２０℃の温度で１〜３回の
ＳＲがなされ、そのＳＲ時間の合計は６〜３０時間の広
範囲に亘る。In the case of extremely thick Cr-Mo low alloy steel with a plate thickness exceeding 100 mm, SR is performed 1 to 3 times at a temperature of 980°C ± 20°C on a boat, and the total SR time is 6 to 30 hours. over a wide range of
ＳＲにおいては、温度が高い程、また同じ温度でも時間
が長い程焼なましの効果は大きく、その程度を示す値と
して次式に示す焼もどしパラメータ〔Ｐ〕が広く用いら
れている。In SR, the higher the temperature or the longer the time at the same temperature, the greater the effect of annealing, and the tempering parameter [P] shown in the following formula is widely used as a value indicating the degree.
（Ｐ） −Ｔ １２０−ＩＪ ｏｇ（ｔ）） ＸＩＯ３
Ｔ−温度（ＯＫ）、を−時間（ｈ「）
一般に、板厚１．００〜３００ｍｍの極厚Ｃｒ−Ｍｏ系
低合金鋼の溶接施工における〔Ｐ〕の範囲は１９．８〜
２１．０になる。(P) -T 120-IJ og(t)) XIO3
T - Temperature (OK), - Time (h'') Generally, the range of [P] in welding of extremely thick Cr-Mo low alloy steel with a plate thickness of 1.00 to 300 mm is 19.8 to 300 mm.
It becomes 21.0.
さらに、溶接金属の靭性および使用中脆化特性に大きく
影響する要因として、溶接金属中の酸素量がある。即ち
長時間ＳＲ後の高温強度を満足し、かつ短時間ＳＲ後の
靭性を確保するとともに、良好な使用中脆化特性を得る
には、溶接金属の低酸素化か必須である。Furthermore, the amount of oxygen in the weld metal is a factor that greatly affects the toughness of the weld metal and its embrittlement properties during use. That is, in order to satisfy high-temperature strength after long-term SR, ensure toughness after short-time SR, and obtain good embrittlement properties during use, it is essential to reduce the oxygen content of the weld metal.
従来、Ｃｒ−Ｍｏ系低合金鋼における高強度化および靭
性改善、さらに使用中脆化特性の改善手段としては特開
昭５３−９５１４ｆｉ号公報や特開昭５８３９１号公報
で開示されているごとく、Ｖ−Ｂ系ワイヤやＴｉ−Ｖ系
ワイヤと高塩基性フラックスとを組合せることが知られ
ている。Conventionally, as a means for increasing the strength and improving the toughness of Cr-Mo based low alloy steel, as well as improving the embrittlement properties during use, as disclosed in JP-A-53-9514FI and JP-A-58391, It is known to combine a V-B wire or a Ti-V wire with a highly basic flux.
しかし、これらはいずれも（Ｐ）が２０．７〜２０，９
の焼なましが大きく進行した後での強度および靭性を問
題としており、その強度は最近の容器の大型化や使用条
件の苛酷化、さらに使用鋼板の高温高圧化に対応できな
いものである。However, all of these have (P) of 20.7 to 20.9
The problem is the strength and toughness after the annealing has progressed significantly, and the strength cannot cope with the recent increase in the size of containers, the harsher usage conditions, and the higher temperatures and pressures of the steel plates used.
また靭性については、短時間ＳＲ条件下、つまりＣＰ）
のより小さな所での靭性確保は困難であった。Regarding toughness, under short-time SR conditions (CP)
It was difficult to ensure toughness in smaller areas.
また、本発明者らか先に特開昭６２−２５９６９５号公
報において、短時間ＳＲ後の靭性、および使用中脆化特
性、長時間ＳＲ後の強度を改善する溶接方法について既
に提案を行ったが、その後の検討によれば短時間ＳＲ後
の強度が高すぎ、水素脆化特性が確保できないことがわ
かった。In addition, the present inventors have already proposed a welding method for improving the toughness after short-time SR, the embrittlement property during use, and the strength after long-time SR in Japanese Patent Application Laid-Open No. 62-259695. However, subsequent studies revealed that the strength after short-term SR was too high, making it impossible to ensure hydrogen embrittlement properties.
（発明が解決しようとする課題）
本発明は、Ｃｒ−Ｍｏ系低合金鋼のザブマージアーク溶
接方法において、従来法の欠点である短時間ＳＲ後の靭
性、使用中脆化特性および水素脆化特性、長時間ＳＲ後
のクリープ破断強度を改善し、良質の溶接部を得る溶接
方法を提供することを目的としている。(Problems to be Solved by the Invention) The present invention solves the problems of toughness after short-time SR, embrittlement properties during use, and hydrogen embrittlement, which are disadvantages of conventional methods, in a submerged arc welding method for Cr-Mo-based low alloy steel. The purpose of the present invention is to provide a welding method that improves the properties and creep rupture strength after long-term SR, and obtains a high-quality weld.
（課題を解決するための手段）
本発明者らは、前記問題点を解決するため、溶接ワイヤ
およびフラックスの両面から検討した結果、短時間ＳＲ
後の靭性および使用中脆化の極めて少ない溶接金属を得
るためには、溶接金属の極低酸素化が必須であることが
わかった。(Means for Solving the Problems) In order to solve the above-mentioned problems, the present inventors investigated both the welding wire and flux, and as a result, the short-time SR
It has been found that in order to obtain a weld metal with extremely low toughness and minimal embrittlement during use, it is essential to make the weld metal extremely low in oxygen.
また水素脆化の少ない溶接金属を得るためには特に短時
間ＳＲ後の強度を低くすること、高いクリープ破断強度
を得るためには長時間ＳＲ後の強度を高くすること、つ
まり８４時間による強度の変化状が小さいことが、水素
脆化特性が良好で、かつ高いクリープ破断強度を得るた
めに必要であることを見い出した。In addition, in order to obtain weld metal with less hydrogen embrittlement, the strength after short-time SR must be lowered, and in order to obtain high creep rupture strength, the strength after long-time SR must be increased, that is, the strength after 84 hours. It has been found that a small change in the amount of change is necessary in order to obtain good hydrogen embrittlement properties and high creep rupture strength.
すなわち、本発明の要旨はＣｒ−Ｍｏ系低合金鋼のサブ
マージアーク溶接方法において、重量％でＣ： ０．０
５〜０．１５％、Ｓ ｉ ： ０．０１〜０．１５％、
Ｍｎ二０．４０〜１．００％、Ｃｒ：１．８０〜３．８
０％、Ｍｏ：０．８０〜１．３０％、を含有するワイヤ
、およびＣａ Ｆ ２１５〜２５％、金属炭酸塩をＣＯ
２に換算して３〜１０％で、かつＳｉ、Ｍｎ、ＡＮの１
種又は２種以上で１．０〜３．５％を含有する焼成型フ
ラックスを用い、さらに下記（Ａ）式で規定されるＶ
： ０．２５〜０．４５％、下記（Ｂ）式で規定される
Ｔ ａ：０．００５〜０．０５％、かつ、Ｖ＋ｌ０Ｔａ
をＯ４０〜０．８０％とすることを特徴とするＣｒ−Ｍ
ｏ系低合金鋼のサブマージアーク溶接方法にある。That is, the gist of the present invention is a submerged arc welding method for Cr-Mo based low alloy steel, in which C: 0.0 in weight%.
5-0.15%, Si: 0.01-0.15%,
Mn2 0.40-1.00%, Cr: 1.80-3.8
Wire containing 0%, Mo: 0.80-1.30%, and CaF 215-25%, CO metal carbonate.
3 to 10% in terms of 2, and 1 of Si, Mn, and AN
A sintered flux containing 1.0 to 3.5% of one or more species is used, and V defined by the following formula (A) is used.
: 0.25 to 0.45%, Ta defined by the following formula (B): 0.005 to 0.05%, and V+l0Ta
Cr-M characterized in that O40 to 0.80%
A submerged arc welding method for O-based low alloy steel.
Ｖ−Ｖ （ワイヤ中）十ｖ（フラックス中）１５・・・
・・・・・・・・・・・・（Ａ）Ｔａ−Ｔａ（ワイヤ中
）＋Ｔａ（フラックス中）１５・・・・・・・・・・・
・・・・（Ｂ）（但し各成分は重量％）
以下本発明の詳細な説明する。V-V (in wire) 10v (in flux) 15...
・・・・・・・・・・・・(A) Ta-Ta (in wire) + Ta (in flux) 15・・・・・・・・・・・・
...(B) (However, each component is % by weight) The present invention will be described in detail below.
まず、本発明においては、ワイヤ成分中Ｃｆｆ１を、０
．０５〜０，１５％とする必要がある。First, in the present invention, Cff1 in the wire component is set to 0.
．． It is necessary to set it to 0.05 to 0.15%.
即ち、Ｃは脱酸性元素として極めて重要であり、適当量
の添加により溶接金属の酸素量を低減するものであるが
、０．０５％未満ではその効果が少なく短時間ＳＲ後の
靭性（以下ｖＥという）、および加速脆化処理後の靭性
（以下ｖＥ十ＳＣという）、さら長時間ＳＲ後のクリー
プ破断強度（以下ＣＲ５という）が低下する。しかし、
０．１５％を超えると溶接時に凝固粒界に偏析しやすく
、高ｄ割れが生ずる傾向となる。In other words, C is extremely important as a deoxidizing element, and when added in an appropriate amount, it reduces the oxygen content of the weld metal, but if it is less than 0.05%, its effect is small and the toughness after short-term SR (hereinafter vE ), the toughness after accelerated embrittlement treatment (hereinafter referred to as vE+SC), and the creep rupture strength after long-time SR (hereinafter referred to as CR5) decrease. but,
If it exceeds 0.15%, it tends to segregate at solidified grain boundaries during welding, and high d cracks tend to occur.
次にワイヤ中のＳＩは０．Ｏ１〜０．１５％とすること
が必要である。Ｓｉは特に使用中脆化特性に影響し、０
．１５％を超えるとｖＥ十ＳＣが低下する。Next, the SI in the wire is 0. It is necessary that O1 to 0.15%. Si particularly affects the embrittlement properties during use, and
．． If it exceeds 15%, vE+SC decreases.
方、０．０１％未満であると、脱酸不足となり、溶接金
属中の酸素量が多くなりｖＥおよびｖＥ＋ＳＣが低下す
る。On the other hand, if it is less than 0.01%, deoxidation will be insufficient, the amount of oxygen in the weld metal will increase, and vE and vE+SC will decrease.
さらにワイヤ中のＭｎは０．４０〜１．００％とするこ
とが必要である。Ｍｎは靭性を確保するために必須であ
るが、一方過多であると使用中脆化を助長する。Furthermore, it is necessary that the Mn content in the wire be 0.40 to 1.00%. Mn is essential to ensure toughness, but too much Mn promotes embrittlement during use.
即ち、０．４０％未満であるとｖＥおよびｖＥ＋ＳＣが
満足せず、一方１，００％を超えるとｖＥ＋ＳＣか低下
する。That is, if it is less than 0.40%, vE and vE+SC will not be satisfied, while if it exceeds 1,00%, vE+SC will decrease.
ところで本発明はＣｒ−Ｍｏ系低合金鋼を対象とするも
のであるから、耐酸化性、耐クリープ性を確保するため
、母材に相当するＣｒおよびＭＯを溶接金属に含有させ
る必要かある。ワイヤ中Ｃｒ１．８０％未満、Ｍｏ０．
８０％未満であると、本発明におけるＣＲＳの向上効果
が得られなくなる。By the way, since the present invention is directed to Cr-Mo based low alloy steel, in order to ensure oxidation resistance and creep resistance, it is necessary to contain Cr and MO, which correspond to the base metal, in the weld metal. Cr in the wire is less than 1.80%, Mo0.
If it is less than 80%, the effect of improving CRS in the present invention cannot be obtained.
しかし、Ｃｒ３．８０％、Ｍｏ１．３０％超では硬化性
が大となり、溶接割れが発生し易くなるとともに、特に
短時間ＳＲ後の加速水素脆化処理後の靭性（以下ｖ Ｅ
＋ Ｈ２という）も低下する。However, if Cr exceeds 3.80% and Mo exceeds 1.30%, the hardenability becomes large and weld cracking is likely to occur, and the toughness (hereinafter referred to as v E
+H2) also decreases.
次に本発明においては組合せフラックスのＣａ Ｆ Ｚ
量を１５〜２５％にすることが必要である。Next, in the present invention, the combined flux Ca F Z
It is necessary to bring the amount to 15-25%.
Ｃａ Ｆ ２量の限定は溶接金属中の酸素量の低減を目
的とするものであるが、溶接金属中の酸素量の低減は溶
接金属の靭性向上に極めて！Ｉｉ要であり、不可欠な事
項である。The purpose of limiting the amount of CaF2 is to reduce the amount of oxygen in the weld metal, but reducing the amount of oxygen in the weld metal greatly improves the toughness of the weld metal! Ii is important and essential.
即ち酸素量の低減は、特に短時間ＳＲ後のｖＥおよびｖ
Ｅ十ＳＣの改善に大きく寄与するものであり、これらの
特性を満足するには、溶接金属中の酸素量としては、は
ぼ２００ｐｐｍ以下であることか必要である。Ｃａ Ｆ
２か１５％未満であると酸素量が高くなり、ｖＥおよ
びｖＥ＋ＳＣが低ドする。In other words, the reduction in the amount of oxygen reduces vE and v especially after short-term SR.
It greatly contributes to the improvement of E1SC, and in order to satisfy these characteristics, the amount of oxygen in the weld metal must be approximately 200 ppm or less. CaF
If it is less than 2 or 15%, the amount of oxygen will be high and vE and vE+SC will be low.
一方２５％超になると酸素量は低くなるちのの溶接中ア
ークか不安定となり、ポックマークか生しビード形状が
不良となる。On the other hand, if it exceeds 25%, although the oxygen content is low, the arc becomes unstable during welding, resulting in pock marks or raw bead shapes.
次に、組合せフラックスはＣａＣ０ＢａＣＯ３３゛
などの金属炭酸塩をＣＯ２に換算して３〜１０％含有す
ることが必要である。Next, the combined flux needs to contain 3 to 10% of a metal carbonate such as CaC0BaCO33 in terms of CO2.
即ち、金属炭酸塩は溶接過程中にアーク空洞中で、ＣＯ
２およびＣＯガスに解離し、アーク空洞中における水素
分圧を下げ溶接金属中の拡散性水素量を低下せしめる効
果を有するためである。That is, the metal carbonate is exposed to CO in the arc cavity during the welding process.
This is because it has the effect of dissociating into 2 and CO gas, lowering the hydrogen partial pressure in the arc cavity and reducing the amount of diffusible hydrogen in the weld metal.
ＣＯ２換算値が３％未満であると溶接金属中の拡散性水
素量が減少せず、水素による低温割れか生じやすくなる
。一方、１０％を超えるとガス発生量が過剰となり、ア
ークが吹上げビード形状が不良となる。If the CO2 equivalent value is less than 3%, the amount of diffusible hydrogen in the weld metal will not decrease, and low-temperature cracking due to hydrogen will likely occur. On the other hand, if it exceeds 10%, the amount of gas generated will be excessive and the arc will blow up, resulting in poor bead shape.
さらに、組合せフラックスはＳｉ、Ｍｎ、ＡρのＩＮ又
は２種以上で１．０〜３，５％を含有する必要がある。Furthermore, the combined flux must contain 1.0 to 3.5% of IN or two or more of Si, Mn, and Aρ.
前述のごとく拡散性水素量を低減する目的で、金属炭酸
塩を含有しているが、ＣＯ２→ＣＯ＋ＯのようにＣＯ２
が分解し、この酸素が溶接金属の酸素量を増加させ、ｖ
ＥおよびｖＥ十ＳＣを低下させる。As mentioned above, metal carbonates are included for the purpose of reducing the amount of diffusible hydrogen, but CO2
decomposes, this oxygen increases the amount of oxygen in the weld metal, and v
Decrease E and vE+SC.
そこで脱酸剤として５１ 、Ｍｎ 、Ａｌｌが必要とな
る。これら１種又は２種以上で１．０％未満では、脱酸
効果が不充分て、ｖＥおよびｖＥ＋ＳＣが低い。Therefore, 51, Mn, and All are required as deoxidizing agents. If the amount of one or more of these is less than 1.0%, the deoxidizing effect will be insufficient and vE and vE+SC will be low.
３．５％を超えると溶接金属中の酸素量は低くなるもの
の、アーク空洞が過度の還元性雰囲気となり、フラック
ス中のＳ Ｉ Ｏ２がＳｌ として、またフラックス中
のＳｌおよびワイヤ中のＳｊかそのまま溶接金属に歩留
り、ｖＥ十ＳＣの低下をもたらす。よってフラックスは
Ｓｉ とＭｎおよびＡρの１種又は２種以上で１．０〜
３．５％である必要かある。If it exceeds 3.5%, the amount of oxygen in the weld metal will be low, but the arc cavity will become an excessively reducing atmosphere, and the S I O2 in the flux will be converted to Sl, and the Sl in the flux and the Sj in the wire will change as they are. This results in a decrease in the weld metal yield and vE+SC. Therefore, the flux is 1.0 to 1.0 or more for one or more of Si, Mn, and Aρ.
Does it need to be 3.5%?
なおそれぞれのフラックス中への形態として、Ｓｉは金
属Ｓｉ、Ｆｅ−Ｓｆ、Ｃａ−Ｓｉ。Note that the Si in each flux is metal Si, Fe-Sf, or Ca-Si.
Ｍｇ２５Ｉで、Ｍｎは金属Ｍｎ 、 Ｆ ｅ−Ｍｎて
、ＡＮ）は金属Ａｇ、Ｆｅ−Ａｌ１．ＡＮ −Ｍｇなと
の金属粉で添加することができる。In Mg25I, Mn is metal Mn, Fe-Mn, AN) is metal Ag, Fe-Al1. It can be added in the form of metal powder such as AN-Mg.
また、本発明に用いるフラックスは、焼成型フラックス
であることが必要であるが、これは本発明に用いられる
フラックス中には金属炭酸塩あるいは、Ｓｉ 、 Ｍｎ
、 Ａｌ１等の金属粉を添加することから、製造中に
高温焼成するシンターフラックスあるいは溶解するメル
トフラックスでは、上記成分の分解あるいは酸化消耗が
起り、品質確保か困難であるためで、この点から低温焼
成（５５０℃以下）の焼成型フラックスであることが必
要である。Further, the flux used in the present invention needs to be a sintered flux, but this is because the flux used in the present invention contains metal carbonates, Si, Mn, etc.
This is because metal powder such as Al1 is added to sinter flux, which is fired at high temperatures during production, or melt flux, which is melted, and the above components are decomposed or consumed by oxidation, making it difficult to ensure quality. It is necessary to use a sintered type flux that is sintered (550° C. or lower).
次に本発明においては、ワイヤおよびフラックスのＶお
よびＴａについて限定することか必要であり、その理由
について以下に述べる。Next, in the present invention, it is necessary to limit the V and Ta of the wire and flux, and the reason for this will be described below.
■はワイヤまたはフラックスの少なくとも一方に添加さ
れる必要があるか、下記〈＾〉式のＶ値を０．２５〜０
．４５％とする必要がある。Is it necessary to add (■) to at least one of the wire or flux?
．． It needs to be 45%.
Ｖ−Ｖ （ワイヤ中）＋Ｖ（フラックス中）１５・・・
・・・・・・・・・・・（Ａ）
０．２５％未満であると、長時間ＳＲ後のＣＲ８か低下
する。また０、４５％を超えると、ＣＲ５は向上するも
のの、短時間ＳＲ後の強度が高すぎｖＥ＋Ｈ２か低下す
る。V-V (in wire) + V (in flux) 15...
・・・・・・・・・・・・(A) If it is less than 0.25%, CR8 after long-term SR will decrease. If it exceeds 0.45%, CR5 improves, but the strength after short-term SR is too high and vE+H2 decreases.
Ｔａはワイヤおよびフラックスの少なくとも一方に添加
させる必要かあるが、下記（Ｂ）式のＴａ値を０．００
５〜０．０５％とする必要がある。It is necessary to add Ta to at least one of the wire and flux, but if the Ta value in the following formula (B) is 0.00
It is necessary to set it to 5-0.05%.
Ｔａ−Ｔａ（ワイヤ中）＋Ｔａ（フラックス中）１５・
・・・・・・・・・・・・・ （Ｂ）０．００５％未満
であると、長時間ＳＲ後のＣＲ３が低下する。また０、
０５％を超えると、ＣＲ５は向上するものの、短時間Ｓ
Ｒ後の強度が高すぎｖ Ｅ 十Ｈ２が低下する。Ta-Ta (in wire) + Ta (in flux) 15.
(B) If it is less than 0.005%, CR3 after long-term SR will decrease. 0 again,
If it exceeds 0.5%, CR5 improves, but S
The strength after R is too high and v E +H2 decreases.
また、前記Ｖ、Ｔａは長日、９間ＳＲでのＣＲ５を確保
し、かつ短時間ＳＲ時のｖ Ｅ 十Ｈ２の点より、特に
適量範囲で共存させる必要かあり、Ｖ＋１、 ＯＴ ａ
を０．３５％〜０．８０％とする必要がある。０．３５
％未満であると長時間ＳＲ後のＣＲ３が低下し、０．７
０％を超えると短時間ＳＲ後のｖ Ｅ ＋ Ｈ２が低下
する。In addition, V and Ta need to coexist in an appropriate amount to ensure CR5 in long-day and 9-hour SR, and v E + H2 in short-time SR, and V + 1, OT a
It is necessary to set it to 0.35% to 0.80%. 0.35
If it is less than %, CR3 after long-term SR will decrease, and 0.7
When it exceeds 0%, v E + H2 after short-term SR decreases.
なお、フラックス中へＶ、Ｔａを含有させるためには、
これらの元素を単体の形で添加してもよく、あるいはま
たＶ２Ｏ５，Ｔａ２０５等の酸化物の形で添加してもよ
い。In addition, in order to contain V and Ta into the flux,
These elements may be added in the form of single substances or in the form of oxides such as V2O5 and Ta205.
前記（Ａ） 、 （Ｂ）式のＶ、Ｔａのフラックスから
の添加時の係数は、溶接金属への歩留りより実験的に求
めたものである。The coefficients when V and Ta are added from the flux in formulas (A) and (B) are experimentally determined from the yield of the weld metal.
なお、その他の微量元素はワイヤ中に以下の範囲で許容
できる。Note that other trace elements are permissible in the wire within the following ranges.
Ｐ≦０．０１２％、Ｓ２Ｏ，０１２％、Ｎｊ ５０．４
０％、Ｃｕ≦０，２０％、Ｎｂ≦０．０２％、さらに、
Ａｓ。P≦0.012%, S2O, 012%, Nj 50.4
0%, Cu≦0.20%, Nb≦0.02%, further,
As.
Ｓｂ、Ｓｎはできるだけ少ないことが好ましい。It is preferable that Sb and Sn be as small as possible.
（実 施 例）
第１表に示す組成の板厚１００關の２１／４Ｃｒ−ＩＭ
ｏ鋼を、第１図に示すＵ満開光とし、第２表に示すｍ成
のワイヤと第３表に示すＭｉ威のフラックスとを種々組
合せ、溶接電流５５０Ａ、溶接電圧３０Ｖ、溶接速度３
０ｃｎ＋／ｌｌ１ｉｎの条件で溶接した。(Example) 21/4Cr-IM with a thickness of 100 and a composition shown in Table 1
O steel was made into U full bloom light as shown in Fig. 1, various combinations of m wire shown in Table 2 and Mi flux shown in Table 3 were used, welding current 550 A, welding voltage 30 V, welding speed 3.
Welding was performed under the condition of 0cn+/ll1in.
尚、第１図中、Ｈ：１００ｍｍ、 ｈ ： ９０１１１
％ Ｄ ： １０＋ｏｍ。In addition, in Fig. 1, H: 100mm, h: 90111
%D: 10+om.
Ｒ：９ｍｍ、θ：３ｅである。R: 9 mm, θ: 3e.
溶接終了後、短時間ＳＲとして温度６９０℃、保持時間
６ｈｒ、ＣＦ３−２０．０１（以下ＳＲＩという）、ま
た長時間ＳＲとして温度７００℃、保持時間２８ｈｒ。After welding, short-time SR was performed at a temperature of 690°C and a holding time of 6 hr, CF3-20.01 (hereinafter referred to as SRI), and long-term SR was performed at a temperature of 700°C and a holding time of 28 hr.
ＣＰ）−２０，８４（以下ＳＲ２という）の２条件のＳ
Ｒを行い、各試験片は、板厚の１／４の部分の溶接金属
部から引張試験片ＪＩＳ Ｚ３１１１ Ａ ２号、衝撃
試験片ＪＩ８２３１１１４号、クリープ破断試験片ＪＩ
ＳＺ２２７２．６．０關φを採取し、各試験に供した。CP) -20,84 (hereinafter referred to as SR2) S of two conditions
R was performed, and each test piece was tested from the welded metal part of 1/4 of the plate thickness to a tensile test piece JIS Z3111 A No. 2, an impact test piece JI8231114, and a creep rupture test piece JI.
SZ2272.6.0 diameter was sampled and used for each test.
また、ＳＲ後の溶接試験片の一部に、第２図に示す条件
のステップクーリングを行い、それよりＳＲしたままの
ものと同様、板厚１／４の部分より衝撃試験片を採取し
、試験を行った。In addition, a part of the welded test piece after SR was subjected to step cooling under the conditions shown in Fig. 2, and an impact test piece was taken from a 1/4th part of the plate thickness, similar to the one after SR. We conducted a test.
なお、このステップクーリングとは、耐使用中脆化を短
時間（約１５日間）で調べる目的で行なわれている加速
脆化処理である。Note that this step cooling is an accelerated embrittlement treatment performed for the purpose of examining embrittlement during use in a short period of time (approximately 15 days).
さらに、耐水素脆化を短時間で調べる目的で、ＳＲ後の
衝撃試験片の一部を６００℃、３００気圧、１００％Ｈ
２の雰囲気で２００ｈｒ保持後試験を行った。Furthermore, in order to quickly investigate hydrogen embrittlement resistance, some of the impact test pieces after SR were tested at 600°C, 300 atm, and 100% H.
The test was carried out after being maintained in the atmosphere of No. 2 for 200 hours.
試験を行った溶接金属の各種性能を第４表に示した。Table 4 shows various performances of the weld metals tested.
第４表にはＳＲＩおよびＳＲ２後の引張強さをＴ Ｓ
（ｋｇ ｆ ／ｍｊ）で、ＳＲ１後の笥撃値、ステップ
クーリング後の衝撃値および水素脆化処理後の衝撃値を
、それぞれ−３０℃での吸収エネルギー（ｋｇｆ・ｍ）
で、さらにＳＲ２後のクリープ破断強度をＣＲＳ （ｋ
ｇｆ／ｍＡ）で示した。Table 4 shows the tensile strength after SRI and SR2.
(kg f/mj), the impact value after SR1, the impact value after step cooling, and the impact value after hydrogen embrittlement treatment are each absorbed energy at -30°C (kgf・m).
Furthermore, the creep rupture strength after SR2 is calculated as CRS (k
gf/mA).
なお、ＣＲＳは試験温度５００℃て３５）ｃｇ ｆ ／
ｍｌ１ｉ。In addition, CRS is 35) cg f / at a test temperature of 500°C.
ml1i.
３０ｋｇｆ／−および２７）ｃｇ ｆ ／−の応力で試
験を行い、４８０℃Ｘ１０５ｈｒの予想破断強度（要求
値≧２４）ｃｇｆ／ｕｌ）を求めた。A test was conducted at a stress of 30 kgf/- and 27) cg f /- to determine the predicted breaking strength (required value ≧ 24 cgf/ul) at 480°C x 105 hr.
これらの結果、本発明の要件を満足するワイヤおよびフ
ラックスの組合せの試験例１〜６は、ＣＲ３が高く、か
つｖＥ、ｖＥ＋ＳＣ，ｖＥ＋Ｈ２の値も良好な値を示し
た。As a result, Test Examples 1 to 6 of wire and flux combinations satisfying the requirements of the present invention had high CR3 and good values for vE, vE+SC, and vE+H2.
比較例中、試験例７は組合せワイヤＷ１のＣが低いため
ｖＥ、ｖＥ十ＳＣおよびＣＲＳか低い。Among the comparative examples, Test Example 7 has low C of the combination wire W1, so vE, vE+SC, and CRS are low.
試験例８は組合せワイヤＷ２のＣが高すぎ、溶接時高温
割れが生したので溶接を中止した。試験例９は組合せワ
イヤＷ３のＳｉおよびＭｎが高すぎるためｖＥ十ＳＣが
悪い。試験例１０はＶが高すぎるため、また試験例１１
はＴａが高すぎるため、ｖ Ｅ ＋ Ｈ２が悪い。試験
例１２はＶが低いため、また試験例１３はＴａが入って
ないためＣＲ５が低い。In Test Example 8, C of the combination wire W2 was too high and hot cracking occurred during welding, so welding was discontinued. In Test Example 9, the Si and Mn of the combination wire W3 are too high, so vE+SC is poor. Test example 10 has too high V, and test example 11
Since Ta is too high, v E + H2 is bad. Test Example 12 has low V, and Test Example 13 does not contain Ta, so CR5 is low.
試験例１４はＶ ＋１０Ｔａが高いためｖ Ｅ 十Ｈ２
か悪い。試験例１５はＶ＋１０Ｔａが低いためＣＲ５が
低い。試験例１６は組合せフラックスＦ１のＣａ Ｆ
２が低いためｖＥおよびｖＥ十ＳＣが悪い。試験例１７
は組合せフラックスＦ２のＣａ Ｆ ２が高すぎ、溶接
中アークが不安定となり、ポックマークも生じたため溶
接を中止した。試験例１８は組合せフラックスＦ４のＣ
Ｏ２が低いため溶接終了後低側れが生じたので機械試験
を中止した。試験例工９は組合せフラックスＦ４のＣＯ
２が高すぎるため溶接中アークが吹上げ、ビード形状が
不良となったので溶接を中止した。試験例２ａは組合せ
フラックスＦ５のＳｔ ＋Ｍｎ ＋ＡＩが低いためｖＥ
およびｖ Ｅ 十Ｈ２か悪い。試験例２１は組合せフラ
ックスＦ６のＳｉ＋Ｍｎ＋ＡＩが高すぎるためｖＥ＋Ｓ
Ｃが悪い。In Test Example 14, V +10Ta is high, so v E + H2
Or bad. Test Example 15 has a low CR5 because V+10Ta is low. Test example 16 is CaF with combination flux F1.
2 is low, so vE and vE+SC are bad. Test example 17
The welding was stopped because the Ca F 2 of the combined flux F2 was too high, the arc became unstable during welding, and pockmarks also appeared. Test example 18 is C of combination flux F4
Due to the low O2 level, low sidewalling occurred after welding was completed, so the mechanical test was discontinued. Test example work 9 is CO of combination flux F4
2 was too high, the arc blew up during welding, and the bead shape became defective, so welding was stopped. Test example 2a has a low St + Mn + AI of the combination flux F5, so vE
and v E ten H2 or bad. In Test Example 21, the Si+Mn+AI of the combination flux F6 was too high, so vE+S
C is bad.
（発明の効果）
以上、実施例にも示されているように、ＣｒＭｏ系低合
金鋼のサブマージアーク溶接において、本発明法によれ
ば、短時間ＳＲ後の靭性、使用中脆化特性および水素脆
化特性が極めて良好で、長時間ＳＲ後においても高いク
リープ破断強度の肩接部が得られ、本発明の工業的価値
は極めて高い。(Effects of the Invention) As shown in the Examples above, in submerged arc welding of CrMo-based low alloy steel, according to the method of the present invention, the toughness after short-time SR, the embrittlement property during use, and the hydrogen The embrittlement properties are extremely good, and shoulder joints with high creep rupture strength can be obtained even after long-term SR, and the industrial value of the present invention is extremely high.
第１図は本発明の実施例に（東１１１した鋼板の開先形
状を示す説明図、第２図は本発明の大施例における加速
脆化熱処理を示す図表である。FIG. 1 is an explanatory diagram showing the groove shape of a steel plate according to an embodiment of the present invention, and FIG. 2 is a chart showing accelerated embrittlement heat treatment in a large embodiment of the present invention.
Claims (1)
いて、 Ｃ：０．０５〜０．１５％（重量％、以下同じ）Ｓｉ：
０．０１〜０．１５％ Ｍｎ：０．４０〜１．００％ Ｃｒ：１．８０〜３．８０％ Ｍｏ：０．８０〜１．３０％ を含有するワイヤ、およびＣａＦ＿２１５〜２５％、金
属炭酸塩をＣＯ＿２に換算して３〜１０％で、かつＳｉ
、Ｍｎ、Ａｌの１種又は２種以上で１．０〜３．５％を
含有する焼成型フラックスを用い、さらに下記（Ａ）式
で規定されるＶ：０．２５〜０．４５％、下記（Ｂ）式
で規定されるＴａ：０．００５〜０．０５％、かつ、Ｖ
＋１０Ｔａを０．３５〜０．８０％とすることを特徴と
するＣｒ−Ｍｏ系低合金鋼のサブマージアーク溶接方法
。 Ｖ＝Ｖ（ワイヤ中）＋Ｖ（フラックス中）／５・・・・
・・・・・・・・・・・（Ａ） Ｔａ−Ｔａ（ワイヤ中）＋Ｔａ（フラックス中）／５・
・・・・・・・・・・・・・・（Ｂ） （但し各成分は重量％）[Claims] In a submerged arc welding method for Cr-Mo based low alloy steel, C: 0.05 to 0.15% (weight %, same hereinafter) Si:
Wire containing 0.01-0.15% Mn: 0.40-1.00% Cr: 1.80-3.80% Mo: 0.80-1.30%, and CaF_215-25%, metal Carbonate is 3-10% in terms of CO_2, and Si
, Mn, and Al, using a sintered flux containing 1.0 to 3.5% of one or more of them, and further V defined by the following formula (A): 0.25 to 0.45%, Ta defined by the following formula (B): 0.005 to 0.05%, and V
A submerged arc welding method for Cr-Mo based low alloy steel, characterized in that +10Ta is 0.35 to 0.80%. V = V (in wire) + V (in flux) / 5...
・・・・・・・・・・・・(A) Ta-Ta (in wire) + Ta (in flux)/5・
・・・・・・・・・・・・・・・(B) (However, each component is weight%)
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP5777090A JPH03258490A (en) | 1990-03-08 | 1990-03-08 | Submerged arc welding of cr-mo low alloy steel |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP5777090A JPH03258490A (en) | 1990-03-08 | 1990-03-08 | Submerged arc welding of cr-mo low alloy steel |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH03258490A true JPH03258490A (en) | 1991-11-18 |
Family
ID=13065112
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP5777090A Pending JPH03258490A (en) | 1990-03-08 | 1990-03-08 | Submerged arc welding of cr-mo low alloy steel |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH03258490A (en) |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP0626227A1 (en) * | 1993-05-24 | 1994-11-30 | KABUSHIKI KAISHA KOBE SEIKO SHO also known as Kobe Steel | Submerged arc welding method for high strength Cr-Mo steel |
| WO2014119197A1 (en) | 2013-02-04 | 2014-08-07 | 株式会社神戸製鋼所 | SUBMERGED ARC WELDING WIRE FOR HIGH-STRENGTH 2.25Cr-1Mo-V STEEL AND WELD METAL |
| EP2610029A4 (en) * | 2010-11-24 | 2016-08-31 | Kobe Steel Ltd | Weld metal and method for submerged arc welding |
-
1990
- 1990-03-08 JP JP5777090A patent/JPH03258490A/en active Pending
Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP0626227A1 (en) * | 1993-05-24 | 1994-11-30 | KABUSHIKI KAISHA KOBE SEIKO SHO also known as Kobe Steel | Submerged arc welding method for high strength Cr-Mo steel |
| US5430269A (en) * | 1993-05-24 | 1995-07-04 | Kabushiki Kaisha Kobe Seiko Sho | Submerged arc welding method for high strength Cr-Mo steel |
| EP2610029A4 (en) * | 2010-11-24 | 2016-08-31 | Kobe Steel Ltd | Weld metal and method for submerged arc welding |
| WO2014119197A1 (en) | 2013-02-04 | 2014-08-07 | 株式会社神戸製鋼所 | SUBMERGED ARC WELDING WIRE FOR HIGH-STRENGTH 2.25Cr-1Mo-V STEEL AND WELD METAL |
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