JPS5925932A - Production of electric welded steel pipe having high strength - Google Patents

Abstract

PURPOSE:To produce an electric welded steel pipe having high strength without losing toughness and weldability, by welding a steel contg. specific compsn. and amt. of C, Mn, Al and >=1 kinds among Nb, V, Ti as a base material to make a pipe, and cooling quickly the weld zone thereof after post annealing. CONSTITUTION:A steel strip 1 consisting of a steel contg. <=0.10wt% C, 0.8- 2.0% Mn, 0.01-0.10% Al, and contg. >=1 kinds among 0.01-0.10% Nb, 0.01- 0.15% V, and 0.01-0.10% Ti as a base material is formed successively to a pipe shape by forming rolls 2 while it is conveyed in an arrow direction. Both ends of the steel 1 are locally heated to a high temp. by a pair of contact tips 3, and the steel is rolled down by squeeze rolls 4, 5, whereby the steel is made into a pipe. The periphery in the weld zone of the steel pipe is heated to an austenite region by a post annealer 6, and is quickly cooled down to about <=200 deg.C at >=30 deg.C/sec cooling rate by a force cooler 7 right thereafter. The pipe is further passed through a water cooling zone 8 and sizer rolls 9, whereby the electric welded steel pipe is obtd.

Description

【発明の詳細な説明】 この発明は、篩強度ＴＬ縫鋼管の製造方法にかかり、と
くにボストアニール加熱域を含む溶接部周辺強度の高い
鋼管の製造に有利な方法についての提案である。DETAILED DESCRIPTION OF THE INVENTION The present invention relates to a method for manufacturing a sieve strength TL stitched steel pipe, and is a proposal for a method that is particularly advantageous for manufacturing a steel pipe with high strength around the welded portion including the boss annealing heating region.

通常、電縫鋼管の製造は、帯状スクールプと称される累
月帯鋼を連続的に管形状に成形１〜だ後、溶゛接すべき
Ｉｉ￥鋼両端をコンタクトチップ−！Ｉ」」ケ導コイル
によって溶接温度寸で加熱し、スフ・ｆズロールにより
その両端を加圧ｌ〜て溶着さ−ける。その後管内外面の
溶接ビードを切削１〜でからボストアニーラ−（ボスト
ヒーデング）と称される後熱処理装置によって溶接部を
局ｇｌ−的に、オースブナイト化の温度域まで加熱する
。ボストに−ル処理後の鋼管は、空冷ゾーンにおいて、
溶接部が４・００〜５００℃以下になる寸で空冷１７、
引きつづいて１・・水冷を施してから簡ちに′リイリ゛
−と称されｌり　′）Ｉ：、形機によって所定の外（１
’＝、−ｊｉｒ’　ＰＨ３とに成形されで１１（Ｊ品と
なる。Normally, in the production of electric resistance welded steel pipes, a graded steel band called a band-shaped scoop is continuously formed into a tube shape, and then both ends of the steel to be welded are connected to a contact tip. It is heated to the welding temperature using a conductive coil, and then welded by applying pressure to both ends using a double roll. Thereafter, the weld bead on the inner and outer surfaces of the tube is cut 1 to 1, and the welded part is locally heated to a temperature range for ausbunite formation using a post-heat treatment device called a Bost annealer. After the boss treatment, the steel pipe is cooled in the air cooling zone.
Air cooling 17 when the welded part is below 4.00-500℃,
Continuing 1. After applying water cooling, it is simply called ``re-iri'')I:, depending on the shape machine, the specified outside (1
'=, -jir' PH3 and 11 (J product).

ところて、最近のラインパイプ用ｔｌ’ｆ、　Ｋ、１鋼
管においては、ますます篩靭１（ｌ：・高強１ｕでかつ
溶接性に・すぐれた鋼管が要望されるようになり、その
〆こめπ（縫鍋管累月としても、低Ｃ化、’＋”ｔｉｔ
　Ｍ　ｎ化のみならず、Ｎｂ、Ｖ、Ｔｉ等の添加によっ
て細粒化、析出強化を図った累月の適用が不可避となり
つつある。すなわち、電縫鋼管とじでｅＪ−１米国石浦
協会（ＡＰＩ）が定めているＡＰＩ規格の５ＬＸ−Ｘ５
２に相当する強度以上のもの、具体的にｂうと、引張強
さ５０　ｋｇ／ｍｍ２、降伏強さ３　Ｇ、６　ｋｅ／ｍ
ｍ２程度以」二の高強隻宣縫鋼管が要求さノ１．ている
１、こうし／こ要求を満足させるには、−に連したよう
に、Ｎｂ、Ｖ、Ｔｉ等を添加してそｉｊら合金元素によ
る結晶粒微卸１化、およびそれらの合〈１λう１．索の
炭化物の折用による強化を図る必要がある。However, in recent years, there has been an increasing demand for tl'f, K, 1 steel pipes for line pipes, which have a sieve toughness of 1 (l), high strength, and excellent weldability. π (as a sewing pot pipe, low C, '+"tit
It is becoming inevitable to apply not only Mn conversion, but also the addition of Nb, V, Ti, etc. to make grains finer and strengthen precipitation. In other words, the eJ-1 is 5LX-X5 of the API standard specified by the Ishiura Institute of America (API) for electric resistance welded steel pipe binding.
2, specifically tensile strength 50 kg/mm2, yield strength 3 G, 6 ke/m
1. High-strength sewn steel pipes of approximately m2 or larger are required. 1. In order to satisfy this requirement, as mentioned in -, Nb, V, Ti, etc. are added to make the crystal grains finer by alloying elements, and their combination 1λu1. It is necessary to strengthen the cables by folding carbide.

ところが、上述のような合金元素を添加した累月による
電縫鋼管においてｔよ、ボストアニール処ＪＭ！および
引き続く夜冷］二程によって、１ｕ、縫溶計１４＋＜１
１周辺のとくにボスｉ・アニール処理＆１−伴つ一１ｇ
じプこそれの熱影響部の軟化が生じ、−’Ｈの結、’４
’−１ｊｌ　４１部と比べて該ボストアニール加熱域の
部分で？、ｉｉ！：μ↓分布の低下を招き易く、ｆＦＪ
：　４：４ご１３との硬（（ＬダＩ；、が大きく庁るた
め、ラインパイプ敷股設Ｈ１上問題が！：１ユじる１：
５０合がある。このような局部的に硬度低］をき／こし
たう・ｒンパイブを使用すると、ラインバイフ軸１送能
率の向上のために管内圧力が増大傾向化しているｌｌ’
ｌ−合においては、硬度の低い溶接部周辺から破Ｊ貨す
る４１故につながる危険（′１がを）乙のみならず、ス
ラリー輸送ラインパイプ等に」パいて（，１、耐＠ｌ（
ｆｌ而面馬ｒ！ｆ’［：　ｔ！ｊ二の観点からも、」−
述１〜た（１ｉｊｊ度低下シ」、大きな技術的問題であ
る。However, when it comes to electric resistance welded steel pipes with the addition of alloying elements such as those mentioned above, Bosto Annealer JM! and subsequent night cooling] by 2 degrees, 1 u, total 14 + < 1
1. Especially around the boss I/annealing & 1-1g
Softening of the heat-affected zone occurs, and -'H results, '4.
'-1jl Compared to 41 parts, in the part of the boss annealing heating area? ,ii! ：μ↓Easy to cause a decrease in distribution, fFJ
: 4:4 There is a problem with the line pipe installation H1 because the hardness ((L da I;) with 13 is greatly affected!
There are 50 go. When a pipe with locally low hardness is used, the pressure inside the pipe tends to increase in order to improve the feed efficiency of the line life shaft 1.
In this case, there is a danger that damage may occur from around the welded part where the hardness is low ('1), as well as damage to slurry transport line pipes, etc.
flJumeba r! f' [: t! From the second point of view,
The above-mentioned (1ijj degree decrease) is a big technical problem.

本発明は、上述した従来技術の欠点ならびにその実情に
鑑み、ＡＰＩ規格のｂＬＸ−Ｘｉ２相′！１′−ソ上の
高強度１ｒｃ　Ｎａｂ鋼管を製造するのにあプｒつで、
靭性や溶接性をＪ（Ｊうことなく溶接部周辺、とりわり
ボス］・アニール加熱域部に：Ｉ）−りる硬ＩＩ１．が
、１υ祠と１”ｌ　勾モジ＜　ｉｊ　ソｉＬ　ＪＪ　１
．　（７）　値７１Ｌ−示−ｊ−，１：　ｒ）’１．　
Ｉｔ　ＬｒＴ：　（ｉＮ　’ｔ７　、、。In view of the drawbacks of the prior art and the actual situation described above, the present invention provides an API standard bLX-Xi two-phase solution! Approximately 1'-1cm high-strength 1rc Nab steel pipes are manufactured using
Toughness and weldability are improved by J (around the weld area, especially the boss) and in the annealing heating area: I) - Hardness II1. However, 1υ Shrine and 1"l Magamoji < ij soiL JJ 1
．． (7) Value 71L-indication-j-, 1: r)'1.
It LrT: (iN't7,,.

を得るのに好適な熱処理法に’１４？艮のある４、シ術
し・−１＞いて提案するものである。'14 on the heat treatment method suitable for obtaining ? This is something I would like to suggest based on the 4, shijutsu technique.

本発明製造方法の／ｉ￥ｆ？（とするところシ：１．　
、７ｆｔ１　％で、Ｏ：　０．］、Ｏｑｔ＋以下、月１
１　：　ｌＪ、８へ−２，０係」、・上びＡｔ：　０．
ｔｌｌ〜（１、Ｉ　０％を含み、かつ＋１　、　（１５
〜＋１　、　、＋　ｆ＋　。/i￥f of the manufacturing method of the present invention? (Whereas: 1.
, 7ft1%, O: 0. ], Oqt+ or less, 1 month
1: lJ, to 8-2, 0 Section'', ・Up At: 0.
tll~(1, including I 0%, and +1, (15
〜+1, ,+f+.

％　（７）　Ｎｂ、０．（１１〜０．１５　ｑｂｃｖ　
ｖ　オｘ　ヒｏ、ｏｔ　−ｏ、Ｊｎ係のＴｉのうちの少
なくとも一１’ｉｌ　Ｓ二２自する側ト〕をＩＵ付とし
た溶接後にボストアニールダＬ１．！ｌ！看−鼾ｒで７
１＞。% (7) Nb, 0. (11~0.15 qbcv
After welding at least one side of the Ti of the v x hi, ot -o, and Jn sections with IU, the boss annealer L1. ! l! 7 with snoring
1>.

縫鋼τ１全製造するに当り、溶接ＦｉＢ周辺ｒｌｌ（Ｓ
Ｈメースデナイト化の＾１ｈＵ域に加熱し、その後面ち
に１１（１：。When manufacturing the entire sewing steel τ1, welded FiB surrounding rll (S
It is heated to the ^1hU range of H maesdenite formation, and then the surface is heated to 11 (1:.

溶接部周辺）１１１分を３０℃／Ｓ８０以」二の速度で
冷却する点の梠゛成にある。以下にその（１゛〜成の詳
細について説明する。The area around the welded part) is cooled at a rate of 30°C/S80 or higher for 111 minutes. The details of (1) to (1) will be explained below.

本発明にかかる製造方法において、′ＰＪ、月であるπ
口；□′Ｆ銀管素４４の化学成分の１服定理由について
ＲＩ？、明する。In the manufacturing method according to the present invention, 'PJ, π which is the moon
Mouth; RI about the reason for taking one of the chemical components of □'F Ginkan Element 44? , reveal.

０はＪｉケも安定して強度を向上させる元素であるが、
０駄の増大は一般に靭性の低下を招き易く、とくに以下
に説明するボストアニーリング後の熱処理方法のような
強制冷却を施す場合には、ＧＭ、、。0 is an element that stably improves strength, but
In general, an increase in OD tends to lead to a decrease in toughness, especially when forced cooling is applied as in the post-bost annealing heat treatment method described below.

が０．１０チを越えれＵＪ：その他の化学成分や冷却６
゛件によっては溶接ｆτ１９が硬化し、かえって靭性の
低下を招くおそ）Ｌがある。もちろん１゛δ接部を強制
冷却する１、ｌ’Ａ合でも、他の化学成分−や管−リー
イズ、造管速１リン、Ｉｃに１．しした適当な冷却条件
を選定すれば、０「Ｉｌがｏ、Ｊｏ％を越えても靭性低
下全防止することは可能と考えられる。しかしながら、
そのｊ（ｊ適糸件の選定はきわめ−Ｃ困難であり、また
たとえ選定できたとしても、その最適冷却条件範囲が狭
く、そのため実際のｔＷ縫溶接製造に適用した場合に不
安定となり易く、かつ溶接部Ｖこ硬（１−〕：〕〜イ乙
Ｌ１−１．−犬′Ｊ−い等の理由から、実際には適用困
頗Ｃ−Ｃ；１２＞る１、そこで本発明においては、溶接
部周辺のＭ、Ｖ　ｌ’ｌ：′ｆ６：ｊｊｌうことなく、
硬度値のみを向」−させる手［りとｌ、　”？：、０限
を０．１０％以下にｔＵｔ定した２、Ｓｉは、鋼中の脱
酸元素とｌ〜てイ〕効ｆｆ元ヌ、−Ｃあるが、過剰に含
有させれば、箪縫溶Ｊ＞、ｚ　Ｉｋ？　Ｉｃ　Ｓ　ｊ−
０２限分によるペネトレークー欠陥がと（鬼りＩＥ　ｔ
−’＼°−ｒく、そのだめ０．８％以下に限定した。exceeds 0.10 cm UJ: Other chemical components and cooling 6
Depending on the circumstances, the weld fτ19 may harden, resulting in a decrease in toughness. Of course, even in the case of forced cooling of the 1゛δ contact part, other chemical components, tube leakage, tube forming speed of 1 phosphorus, Ic and 1. If appropriate cooling conditions are selected, it is considered possible to completely prevent a decrease in toughness even if Il exceeds o, Jo%.However,
It is extremely difficult to select a suitable thread, and even if it could be selected, the range of optimal cooling conditions would be narrow, so it would likely become unstable when applied to actual TW sewing welding manufacturing. And for reasons such as the hardness of the welded part V (1-):]~I L1-1. , without M, V l'l:'f6:jjl around the weld,
The 0 limit was set to 0.10% or less2, Si is the deoxidizing element in steel and the effect factor There is -C, but if it is contained in excess, it will melt J>, z Ik? Ic S j-
Penetration defect due to 02 period (Oniri IE t
-'\°-r Therefore, it was limited to 0.8% or less.

）４ｎｌｌｉ、Ｃと同様に鋼質の強ロＬ−ｆ、′向−１
さ＝田る元素であって、靭性１央％Ｖこも＠”Ａｌ）−
ご）ンン）カー、０．乏）悌未満ではＡＰＩ規格５　Ｌ
Ｘ　−Ｘ　５２相）！ｒ＋　０．）弓：＋ｉ　Ｌｔｔ力
；イｑられす、一方過剰にＩｎ奮添力＋ｌ　Ｌ、　／、
Ｌ場合ｅヒｋ」１、Ｍ、ｎＯ酸成分主体としたペネトレ
ーターク＜　ｌ’ｌｉ’＋　７５ζ５色々快しやすくな
るとともに、９蚤１１１１　？ｉ７人１１＆こ、ｌ：　
ｈ悠！ｈ人玄ｊノ果によって靭性劣化金招きやすくなり
、こｔｌ、らのＪ耳」　由　か　ら　Ｍｎ　　＃Ｌ　　
ｔ：Ｊ、’　　０．８　〜２．０　　％　　Ｗ−ＩＩＪ
　　シｉｉ　１．ｚ　　ノこ　。) 4nlli, similar to C, strong steel L-f, 'direction-1
It is an element with a toughness of 1 center%V @”Al)-
Go)nnn)car, 0. API standard 5 L for less than 悌
X −X 52 phases)! r+0. ) Bow: +i Ltt force; EQ, while excessively exerting force +l L, /,
L case ehik' 1, M, nO Penetration arc mainly composed of acid components <l'li'+ 75ζ5 It becomes easier to enjoy various things, and 9 flea 1111? i7 people 11 & ko, l:
h Yu! Due to the fruit of the human race, the toughness deteriorates and it becomes easy to cause gold, and this causes the J ear from Mn ＃L.
t: J, '0.8 ~ 2.0% W-IIJ
Ciii 1. Z Noko.

ｈｔね、銅の脱酸元素として不ｊ効な元素−Ｃ扶９す、
まだ結晶杭機Ｒ１１１化作用により、鋼のダｌｊ　１ｌ
ＳＬ、　ｑｉＴＪ　（Ｉｌ苓：１ｉ１　ｕ二さぜるが、
０．１０％を越え７＋、）、！、〃）乏−ってｖツノｆ
１−全低下させるばかりでなく、溶接性をも低下きせる
ことがら、上限を０．１０％としだ。ht, an element that is ineffective as a deoxidizing element for copper - C F9,
Due to the action of crystal pile machine R111, the steel pile machine R111
SL, qiTJ
More than 0.10% 7+,),! , 〃) Scarcity-te v Tsuno f
1- The upper limit is set at 0.10% because it not only reduces the total content but also reduces weldability.

さらに本発明の対象とするＴ１７．縫銅管Ｑ」４、ＡＰ
Ｉノ２１１格の５　ＬＸ　−Ｘ　ｌ’ｉ２相尚以」二の
強度苓：有するものとするため、前記各成分のほか、Ｎ
ｂ、ＶおよびＴ土のうちの１イ重ま／こは２１Ｔｉ以」
−な・含イｊネせて、これらの元素による結晶粒微細化
効果と４１ｉ出効果による累月強度の向上を図る。こｉ
＋らの元素の成分限定範囲は次のとおシであＺ）。Furthermore, T17. which is the object of the present invention. Sewn copper pipe Q"4, AP
In addition to each of the above components, N
1 of B, V and T soil is 21Ti or more.
- By including rice, the grain refinement effect of these elements and the 41i output effect improve the crystal strength. Koi
The limited range of ingredients for the elements listed above is as follows.

Ｎｂｉ＃Ｊ、、０　、　（１１％未満では前記効果が不
充のであり、一方０１０％を越えればかえって靭性４・
劣化させることから、０．０１〜０．１０係に限定した
。Nbi#J,,0, (If it is less than 11%, the above effect is insufficient, while if it exceeds 0.10%, the toughness will be reduced by 4.
Since it causes deterioration, it is limited to a ratio of 0.01 to 0.10.

■は、Ｎｂと同様に０．０１％未満では前記効果が不十
分であり、一方０．１．５％を越え）１．ばかえって靭
性を劣化させるから、０．０１〜［１、］　５％に限定
した。(2) As with Nb, if it is less than 0.01%, the above effect is insufficient; on the other hand, if it exceeds 0.1.5%) 1. Since it would actually deteriorate the toughness, it was limited to 0.01 to [1,] 5%.

Ｔ１は、Ｎｂ、Ｖと同様ニ０　、　ｆｌ　１　％　；、
１’：　ｉｉｌ’ｊ　テｔｌＪ、１）ｉＪ　記効果が不
充分であり、一方〇　、　１．０　％　ｆ　Ｊ：’Ｓｔ
えノ１は靭性全劣化させるぽかりでなく、溶接に１をも
低−１・さぜるから、Ｔ１含有盾１：　１ｊＨＯ，（１
１〜０．１０チに限定した。Similar to Nb and V, T1 is 20, fl 1%;
1': iil'j TetlJ, 1) iJ The effect is insufficient, while 〇, 1.0% f J:'St
Eno 1 does not completely deteriorate the toughness, but also causes 1 to be low-1 in welding, so T1-containing shield 1: 1jHO, (1
It was limited to 1 to 0.10 inches.

なお、この発明の方法におい＝ｃ　＆；Ｉ：、通常ｉ＋
、ｌ’、　Ｊｕｌ　、Ｉボのように主としてＡＰＩ却、
格のｉ　Ｌ　Ｘ　−Ｘ、　５２　ニ相当する強度以−１
−の強１す４−打する’ｉｌｉ、　４ｉ’ｌＩぐ（・判
１１′（を対象とする。その理由は、ＡＰＩ却格１’ｌ
ＬＸ、　　Ｘ５２相当強度よりも低強度のｆｆ１Ｙ鋳鋼
管で（よ通’ｌｊｆ　Ｎ　ｌ）　、　Ｖ。In addition, in the method of this invention =c &;I:, usually i+
, l', Jul, Ibo, mainly API-based,
case i L
'ili, 4i'lIgu(・ban11'), which is played by strong 1s 4-, is targeted.The reason is that the API negative case 1'l
LX, FF1Y cast steel pipe with lower strength than X52 equivalent strength (Yotong'ljf Nl), V.

Ｔ：Ｌｈｆ３の合金元素の添加シｌ、ないので、もとも
と仁ノ１．ら合金元素による＃ｌｌｌ　Ｊ立化耘よび４
１ｉ出り・１１化きノ１．だ累月がΦ件とされるものと
は熱処理による効果が要るからである。すなわら低強度
１ｒ１，０鋼９ｊ１に夕・４する’Ｉｆｆ、縫部接部の
ボストアニール処理に−１，−いて＆、Ｉ１、整粒化効
果により他の部分と孔中９し−Ｃ却りて溶１長部の方７
１１弓！１１度、靭性の向」二がＱ」−からノ）５、そ
の／７−め本発明のような強制冷却処理が全く不問とｆ
ｌイ）のである。T: Since there is no addition of alloying elements in Lhf3, it was originally Nichino1. #llll by alloying element
1i release/11th version 1. This is because the effect of heat treatment is required for the Φ condition. In other words, if the low strength 1r1,0 steel 9j1 is applied to the steel 9j1, -1, - is applied to the boss annealing treatment at the seam contact area, -1 is applied to the bottom annealing treatment at the seam contact area, and the hole is combined with other parts due to the grain size adjustment effect. On the contrary, Soru 1 Nagabe 7
11 bows! 11 degrees, the direction of toughness "2" - to 5)
lb).

次に、上述のよ″″５カ素、ＩＡ金用いで、不発りＪ興
造方法についての工穆を図面に上りｉ仔細にｉｉ（？、
１．１１１−Ｊる。Next, using the above-mentioned ``5'' elements and IA gold, we went up to the drawings and detailed the construction method for the unexploded J production method (?,
1.111-Jru.

ハ′ろ１図は、本発明のボストアニール熱処理力法を適
用した市、縫鋼管の製造エイＨＩＨ看、、　４９□Ｌ略
的に承りものであり、１イ１．予ｔｌｉｌ　’Ｉ’！の
素材となる’：ｉ）釘ｒ・ｌ　Ｊ　＆−１１戊形Ｉ】−
ル２により順次管伏に成形さ：ｈＪ：１τ５、−タ□・
１のコンタクトチツフ゛３（接庁１！−了）もしく　ｉ
Ｊ訪＞−Ｑ；力１１パノ〜コイルにより、溶接すべきｌ
’ｊ　ｆＴｌ・弓両端が局Ｔ’）１１’ｌ’Ｊ　’／’
Ｘ　＋髪イ、１品に加ｐ４１され、続いてスクイズＩＵ
−／し４．　、　ｈ　ｔＤ　ＨＥ、　−Ｆに、しりその
イｉｙ鋼両側が溶接部Ｍ１ｆされ、電縫１角管ＪＡとη
る。その後、’Ｉｌｌ　Ｌ’ｈ　ｊＰ、　’ｉｊ（Ｉ　
Ａの溶接部−：　Ｂｊスト”に−ラー（後熱処理装置）
（１Ｇで上り）吊）τｌ（ｒ＋勺にオースブナイト化ｌ
Ｖ＋’＋度に加熱１．ｌ’ｌ；鈍さり、る１、ここで従
来の通常り凡ｌ二程でｔ、１−、ボストアニール１図の
仮想線で示す空冷ゾーンＺＫふ・いて溶ｊ妾ε１１へが
４．　（１　０〜５　Ｑ　（１　℃り下と〃る′まで空
冷ネｉ１．、その後水冷ゾーン８において水冷され、直
ちに一す°イザーと称する定形機１）により所定の外径
、真１”Ｊ　１．Ｗに成形さノ１，て製品となるので．
４Ｂる。Figure 1 is a schematic representation of the manufacture of sewn steel pipes using the boss annealing heat treatment method of the present invention. Pretlil 'I'! ': i) Nail r・l J &-11 戊形I】-
Formed into a tube in sequence by 2: hJ: 1τ5, -ta □・
1 contact chip 3 (contact 1! - completed) or i
J >-Q; Force 11 - L to be welded by the coil
'j fTl・Both ends of the bow are station T') 11'l'J '/'
X + Hair I, 1 item added p41, followed by squeeze IU
-/shi4. , h tD HE, -F, both sides of the steel are welded M1f, and the ERW rectangular tube JA and η
Ru. Then 'Ill L'h jP, 'ij(I
Welded part of A: Bj strike'' (post-heat treatment equipment)
(up at 1G) τl (ausbunite on r +
Heat to V+'+ degrees 1. l'l; dullness, 1, here about 12 times as in the conventional case, t, 1-, and the air cooling zone ZK shown by the imaginary line in the boss annealing 1 flow to the welding concubine ε11; 4. (10 to 5 1.The product is molded into W.
4Bru.

とれに対し、本発明方法の場合、主として１旧妾時のＩ
ＬＡＺ’に調整するだめに行うボストアニーラー（！に
よりその溶接鋼管を再びメーステナ−（　＋・イし温度
まで加熱することに伴う？ｔｉ’，縫鋼管］．　Ａ　１
１２）淫ｆ接部周辺；すなわちボストアニール熱影Ｍｖ
ＵＢを含む部分全体を、ボストアニーラ−６Ｖこ近ねこ
してｊｉｔ’．　ｌｉｆｔさノ］，た強制冷却袋ｒｒＬ
７により、従来のよりなり，＋５．　／／ｂを廃して直
ちに３０℃／　ｓ　ｅｃ　ｕ）、　、−ｌの？′１１却
辻１扶で強制冷却し、その後前配り・１ザ−前の水冷ゾ
ーン８によりさらに水冷して定形機１）により成形する
。In contrast, in the case of the method of the present invention, I mainly
The welded steel pipe is heated to LAZ' by the boss annealer (!) and then the welded steel pipe is heated to the temperature of ?ti', the welded steel pipe]. A 1
12) Around the indecent f contact area; that is, the boss annealing heat shadow Mv
Rub the entire part including the UB near the Bost Annealer 6V and jit'. lift sano], forced cooling bag rrL
7 makes it more conventional, +5. //30℃/secu), , -l immediately after disposing of b? The product is forcedly cooled in the cooling zone 1, and then further water cooled in the water cooling zone 8 at the front of the sheet and molded in the shaping machine 1).

、に述のようなオーステティ１化／ｌｌ＋ｉｉ　ｌ！Ｉ
以−１げ，加熱し２だ後８　（１　℃／ｓｅａ以−ｌこ
の冷却速ｌＩＪＩで１゛１つ強制冷却は、オースブナイ
ト化７ｊ＋Ｎｔ度以上．に加熱後ｊ（ｊ　ｊりに実施す
ることが必要である。その強制冷却時期が遅く力るほど
細粒化効果、焼入効果が低減し、溶接部周辺の硬ＩＷ値
の向」二が期ｆ−“ｒ　シｆｉｌ＋くなるｎ　ＪＬ体的
ニハ、溶Ｗ　ｆｉｌｓ　〕ｚ：Ｍ　Ｌｌｊ　カ９　０　
（１　℃Ｊ：りも低イＣ：ｕ’ｔ　ｌ−’Ｊに低下する
以前の段階でｉｉＪ及的速やかに強制冷却を開始するこ
とが望′ましφ。, as described in Austety 1/ll+ii l! I
After heating, 8 (1 °C/sea or more), at this cooling rate lIJI, forced cooling should be carried out after heating to more than 7j + Nt degrees of ausbunitization. The later the forced cooling time is, the more the grain refining effect and quenching effect are reduced, and the hardness IW value around the weld area becomes worse. Target niha, melting W fils]z:M Llj Ka9 0
(It is desirable to start forced cooling as soon as possible before the temperature drops to 1°CJ: 1°C: u't l-'J).

このような加熱処理偵後の強制冷却による溶接部の１却
曲線の一例を、従来法すなわちメーステプイト化温問以
」二に加熱後面ちに強制？１１却苓Ｔ１ｊつことなく一
旦空冷を行う場合の冷却曲χ，１ｊ１の一例と比較して
第２図に示す。但し、１１５２図の伶却曲線ｔよ、外径
５　０．　８　ｍｍ、肉’Ｒ．　９　、　５　２　ｎ１
１ｎの′ｆ１１、縫階臂ヲ２　４、　ｍ／ｌｎｉｎＯ造
管速度（すなわちＴ１の几Ｔｊ；ｉｌｉ　ｌｔＪｆ　）
で製造１７た場合について示す。An example of such a curve of a welded part due to forced cooling after heat treatment is compared to the conventional method, that is, the forced cooling after heating. FIG. 2 shows a comparison with an example of the cooling curve χ,1j1 in the case where air cooling is performed once without cooling. However, according to the bending curve t in Figure 1152, the outer diameter is 50. 8 mm, meat 'R. 9, 5 2 n1
'f11 of 1n, suture angle 2 4, m/lninO pipe forming speed (i.e. T1's Tj; ili ltJf)
The case of manufacturing 17 is shown below.

力お前述のように、ｔ’ｌｉ制冷却速度全３０℃りｓｅ
ｃ以−１に設定する必要があることか」、本発明者等の
詳細ｆＩ史験により見出さｉ′１．たことであり、その
実験結果の一例をｆｌ’＋　３図に示す。この第３図ｔ
、１−２後述する実施例の試別番号Ｅの累月について、
加熱処理的後の強ｉｌｉ’ｌ冷却速世を神／ｚ変化婆せ
た場合の冷ノ５１１速度が溶接部のボストアニール処理
に伴って什ず２）七の熱形！１予部硬Ｉに及はす影〜・
２シ全〉Ｊテすものである。この第：３図から強制冷却
速度企１３（１℃／ｓｅａ以」二とすることによシ溶接
１４１（の６史毘を５力、激に向」ニさせ得ることがｆ
ｙＪらかである、。As mentioned above, the total cooling rate is 30℃
Is it necessary to set i'1. An example of the experimental results is shown in Figure fl'+3. This figure 3
, 1-2 Regarding the cumulative months of trial number E in the example described below,
511 speed of cold when the strong cooling speed after heat treatment is increased/z changes due to the boss annealing treatment of the weld 2) Seven heat forms! 1 Shadow that extends to the hard part I~・
2〉Jte. From this Figure 3, it is found that by increasing the forced cooling rate to 1°C/sea or more, it is possible to greatly increase the 6-year history of welding 141.
yJ is easy.

′１／こ、加熱処理白抜の強ｆｌｉｌｌ冷却におりる冷
却につ了１１、−の温１則なよ、可及的に低く〃ること
か望はしく、本発明者等の実験によれば、２　（１１１
１−：以−「寸で強＋１＋１１冷却することが望゛まし
いことが２目ｊ明した。その強制冷却の具体的手段は任
意であり、水冷噴Ｉ劣水？ｊｔ、シャワー水冷、強制空
冷等のいずれでも良い。'1/This is the temperature of the heat treated white spot during intense cooling. According to 2 (111
1-: From now on, it has become clear that it is desirable to perform strong +1+11 cooling.The specific means of forced cooling is arbitrary, and water cooling jets, shower water cooling, and forced cooling are optional. Any method such as air cooling may be used.

そしてまた強制冷却における３０℃／ＳｅＣ以」二の範
囲の具体的冷却速度や冷却帯の長さなども、対象となる
Ｔ［；、付備管等のサイズ、板ｊ１，１、；Ｉ゛：、　
（Ｉｆｆ速ＩＷに応じで適宜選定すればよい。In addition, the specific cooling rate in the range of 30℃/SeC or higher in forced cooling, the length of the cooling zone, etc. :,
(It may be selected as appropriate depending on the If speed IW.

以下不発ツの実施例につい（説明する。Examples of failures will be explained below.

第１表の試料記号Ａ−Ｉに示される化学戊分を有する供
試制を用い、各押簑強凹を１Ｊる外径５０Ｂｍｍ、肉厚
１．５２ｍｍの電縫鋼管を造管速度２４ｍ／ｍｊｎで製
造した。ボスドアー−１処！ｔおける加熱温度は８２０
℃とし、その後、的ちに３０℃／ｓｅｏ以上の冷却速度
で水冷した、世し、実際、の水冷開始詩の溶接部温間９
００℃であった。また、強制水冷ゾーンの長さは６〜８
ｍどし、水冷終了時の温間が２００℃以−となるしう設
定して強１１ｉ１１冷却した。Using the test system with the chemical fraction shown in sample symbol A-I in Table 1, an electric resistance welded steel pipe with an outer diameter of 50 Bmm and a wall thickness of 1.52 mm with each sump recess of 1 J was produced at a pipe manufacturing speed of 24 m/min. Manufactured by mjn. Boss door - 1st place! The heating temperature at t is 820
℃, and then immediately water-cooled at a cooling rate of 30℃/seo or more, in fact, the welding part warm 9
It was 00℃. In addition, the length of the forced water cooling zone is 6 to 8
The temperature was set so that the temperature at the end of water cooling was 200° C. or higher, and strong cooling was performed.

なお比較例として、前記同一のイエ１．１１・（４３Ａ
〜ＩＩ　ｆｃついて、加熱処理ＩＩ′ｊ後に強制冷却−
１ｌ−ずに′まず待冷し、４・０（）〜５００℃以下と
なってからＵ」じめてライザτ前の水冷ゾーンにおい−
こ水？９しでη’ｊ　’ｌ’？　Ｌ／た。As a comparative example, the same house 1.11 (43A
~II fc, forced cooling after heat treatment II'j-
1L - First, let it cool down, and wait until the temperature is below 4.0 () ~ 500℃, then enter the water cooling zone in front of the riser τ for the first time.
Water? 9 and η'j 'l'? L/ta.

ヒ配実ｂ（（−例および比軸例ｖｃ　Ａ、−’　−Ｃ’
ｔ！’）　Ｆ＞ノまた名′ｉ１（付備管について、管１
υ４１部と溶接Ｆｉｌｉの硬度ｊ１゛、と管溶接部の周
方向引張強度の関係をｎｒｒａべ／こπｌ’ｌ　：４１
’：を第４図に７Ｊ′：、す。第４図から明らかなよう
に、加熱処理直後に強制冷却を行わない比軟例【′こ＾
）１書」°、ｆｔｌ４４部と溶Ｊ＄　Ｉ’ｌｌの硬度差
−はビッカース硬度で約２０〜１・０どｒ（ｙ　打１　
ｊ？ｌ（の？＋ｉｌｉ度が低くなっているが、強制？／
ｌｊ却処理により、ＩＵ　４，１　ｊ’、１１と溶接Ｅ
τ１１の硬曳差Ｖ、１．著しく低亦冒７、≠）合によっ
てＣ１溶接部の硬度の力が」二列−ノるととが昭められ
る。。hypothetical fruit b ((-example and ratio axis example vc A, -'-C'
T! )
The relationship between the hardness of the υ41 part, the hardness of the weld Fili, and the circumferential tensile strength of the pipe weld is nrra/koπl'l: 41
': is shown in Figure 4 as 7J':. As is clear from Fig. 4, the ratio soft case ['ko^^
) 1" °, the difference in hardness between 44 parts of ftl and molten J$ I'll is about 20 to 1.0 dor (y 1
j? l(?+ili degree is low, but is it forced?/
IU 4, 1 j', 11 and weld E
Hardness difference V of τ11, 1. Due to the extremely low resistance 7,≠), the hardness of the C1 weld is reduced to 2-row. .

η」、前Ｊホの実ｈｔｌｉセ１１においてｔ：ｌ、１）
２０℃の加熱処理部だだしに水？９を開始し、実際の水
冷開始部勺に４；す２）溶ｊν部乙！？ｔ　ｌ彫）Ｊ：
　＋１０　＋、１℃となっていた。η'', t:l, 1 in the previous Jho no real htli se 11)
Water in the 20℃ heat treatment section? Start 9 and move on to the actual water cooling start section 4; ? t l carving) J:
It was +10+, 1℃.

−刀、比較のためり２０℃から６００℃′までを自然）
Ｊ’ｌ　？’６１−、　Ａｘ　７Ｊニー（ｉ　０　（１
℃カラ：（０℃／　ｓ　ｅｃ　ＪＲ，−１ｘ　］冷却８
１１１−１１”で６・′１２制冷ノ、１１全ｂ’ｉｌｊ
　１．、てみたが、この場合匠−ＩＪ−溶１′）↓部の
イ＋ｌＩ！ＩＪＩ向−１−効北（」、はとんど認めらＪ
ｌなかつ／ζ。-Sword, natural temperature from 20℃ to 600℃' for comparison)
J'l? '61-, Ax 7J knee (i 0 (1
℃ empty: (0℃/sec JR, -1x] Cooling 8
111-11" with 6/'12 cooling, 11 all b'ilj
1. , but in this case Takumi-IJ-R1') ↓ part I+lI! IJI direction - 1 - effect north ('', Hatondo admitted J
l Nakatsu/ζ.

このことから本発明の効果を充り〕に発揮窩ぜるために
ｔ、ｌｌ、−４−ステプイト化温世以上への加熱処理後
、ｉ１ｊ及的速やかに強制？Ｃ却を開始する必四）があ
ることが１．ｌｉＩらかである。Therefore, in order to maximize the effects of the present invention, it is necessary to force the heat treatment to a temperature higher than t, ll, -4-steppeitization temperature as soon as possible. 1. It is necessary to start C-rejection. liI is clear.

”：’−−Ｌ、　ｎｊｉ、　ｊ’ｊｌ　Ｌだように本発
明により、溶接部周辺２〈に２ｊζストアニールに伴う
その熱形み’ｌ’　ｌ；Ｂの（１１１ｊ度低下全防市す
ることができ、したがって高αＬ１と・面ＹＩＪ　１′
ｌ苓二Ｉ片求きれる１１１縫鋼管どしてイハ頼性が、（
−ラい１［シ付備９？をイ（Ｊることができ、／ｉ、ｌ
ｉに１“、１″口〕」月−１・で使用されるラインパイ
プ用の１１１．縫（ｐ・；９゛ｆと１．、−Ｃ１（＋１
１ＪＪ・：ζ律故に至るおそれのない”Ｃ１３：　ｊ％
　（？ｐＩ管企ｉｎ　Ｚ）ξとができる。'':'--L, nji, j'jl According to the present invention, the heat forming caused by the 2jζ store annealing in the vicinity of the welded part 2 is reduced by 111 degrees. Therefore, with high αL1 and plane YIJ 1'
The reliability of the 111 sewn steel pipe that can be obtained is very high (
-Rai 1 [Si appendix 9? i (J can be /i, l
1", 1" for the line pipe used in month-1. Sewing (p・;9゛f and 1., -C1 (+1
1JJ: There is no risk of this occurring due to the ζ law” C13: j%
(?pI control plan in Z) ξ is possible.

４・図１１１の簡単ｆｒ、説明 第１図は、この発明の熱処理方７ノー４・適用１．た１
１Ｘ。4・Simple fr in FIG. 111, explanation FIG. 1 shows the heat treatment method 7 of this invention No. 4・Application 1. Ta1
1X.

付備管のｆＪｌ１４造工４！Ｉ！丘：　１ｆｆ４略的に
示ず路線図、Ｂ（１２図ｔ」５、加熱処理Ｕ・の伶却曲
イ、ｌｉＩの−・例を示すグラフ、 第７３図は、加熱処理後の強制？′１１却速１田全ｑｉ
ｌｉ々勿化させたときの母４１部と溶接部の（１１！ｌ
（１，’　ｐ、’ｊ　ｋ　７ｉ＜−Ｊグラフ、 ε（５４図は、本発明法と従来ｌ）、姓ユ４．し）２）
　Ｉｔ、Ｉ：　４４　Ｆ！ｌ九と溶接部の硬度差と溶接
ｒＸ＋′Ｉ周方向引すＩシ強１０−の関係４示すグラフ
である。Additional pipe fJl14 construction 4! I! Hill: 1ff4 Route map (not shown schematically), B (Figure 12) 5, Graph showing an example of heat treatment U. 11 rejection speed 1 field qi
The mother part 41 and the weld part (11!
(1,'p,'j k 7i<-J graph, ε (Figure 54 shows the method of the present invention and the conventional method), surname Yu4.shi)2)
It, I: 44 F! 4 is a graph showing the relationship between l9, the hardness difference of the welded part, and the weld rX+'I circumferential pulling strength 10-.

１・・累月帯鋼、ＩＡ−・市、耕銅７７．２−フィンパ
スロール、３　・コンタクトナツツ、４．　スフ・イズ
トツブロール、ｂ・・スクイズリ（Ｆ　ｒｌ−ル、ｔ）
・・・ボストアニーラ−１７・・強制冷却づ・＞　ｌｒ
’ｆ、８・・水冷ゾーン、！１・・パリイサーロール。1. Monthly band steel, IA- City, Copper 77.2-Finpass roll, 3. Contact nuts, 4. Suf Iztotubrol, b... Squeezeli (F rl-le, t)
・・・Boss annealer-17・・Forced cooling・＞lr
'f, 8... water cooling zone! 1. Pariisa roll.

第１図 第２図Figure 1 Figure 2

Claims (1)

【特許請求の範囲】 Ｊ　重ＶＬ％で、Ｏ：　０．１０　％以下、Ｍｎ　：　
（１，８〜２．０％およびＡｔ：　０．０］〜０．１０
チを含み、かつ０．Ｏ］〜（１，１０係のＮｂ　、　　
０．０１〜０，１５％の■および０．０１〜０．１（ｉ
　％のＴｉのうち少なくとも一鍾を含有する鋼を−ＩＵ
材として溶接後にボストアニール処理を経て？ｌＬ縫鋼
管を製造するに肖り、 溶接部周辺を、オースブナイト化の温度領域に加熱し、
その後直ちに」二ｊ’ｊＬ溶接部周辺部分を８０℃／ｓ
ｅａ以−ヒの速度で冷却することを特徴とする篩強度電
縫鋼管の製造方法。[Claims] J Heavy VL%, O: 0.10% or less, Mn:
(1,8-2.0% and At: 0.0]-0.10
and 0. O] ~ (Nb of the 1st and 10th section,
0.01-0.15% ■ and 0.01-0.1(i
-IU of steel containing at least one part of Ti
Is the material subjected to boss annealing treatment after welding? In order to manufacture lL sewn steel pipes, the area around the welded area is heated to a temperature range that produces ausbunite.
Immediately thereafter, heat the area around the welded area at 80°C/s.
A method for manufacturing a sieve-strength electric resistance welded steel pipe, characterized in that it is cooled at a rate of ea-hi.