JPH0192320A - Improvement of toughness of joint of high tension steel subjected to flash butt welding - Google Patents
Improvement of toughness of joint of high tension steel subjected to flash butt weldingInfo
- Publication number
- JPH0192320A JPH0192320A JP24814887A JP24814887A JPH0192320A JP H0192320 A JPH0192320 A JP H0192320A JP 24814887 A JP24814887 A JP 24814887A JP 24814887 A JP24814887 A JP 24814887A JP H0192320 A JPH0192320 A JP H0192320A
- Authority
- JP
- Japan
- Prior art keywords
- joint
- toughness
- butt welding
- flash butt
- high tension
- 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
- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 31
- 239000010959 steel Substances 0.000 title claims abstract description 31
- 238000003466 welding Methods 0.000 title claims abstract description 30
- 238000001816 cooling Methods 0.000 claims abstract description 18
- 238000010438 heat treatment Methods 0.000 claims abstract description 13
- 229910052758 niobium Inorganic materials 0.000 claims abstract description 9
- 229910052720 vanadium Inorganic materials 0.000 claims abstract description 9
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 6
- 229910052759 nickel Inorganic materials 0.000 claims abstract description 4
- 238000000034 method Methods 0.000 claims description 10
- 239000000203 mixture Substances 0.000 claims description 7
- 230000000694 effects Effects 0.000 abstract description 6
- 229910052799 carbon Inorganic materials 0.000 abstract description 4
- 229910052802 copper Inorganic materials 0.000 abstract description 2
- 238000007670 refining Methods 0.000 abstract 1
- 239000013078 crystal Substances 0.000 description 6
- 239000000463 material Substances 0.000 description 5
- 229910001566 austenite Inorganic materials 0.000 description 4
- 239000010953 base metal Substances 0.000 description 4
- 238000009826 distribution Methods 0.000 description 3
- 238000005261 decarburization Methods 0.000 description 2
- 238000009792 diffusion process Methods 0.000 description 2
- 238000001953 recrystallisation Methods 0.000 description 2
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 1
- 229910001563 bainite Inorganic materials 0.000 description 1
- 230000007423 decrease Effects 0.000 description 1
- 230000006866 deterioration Effects 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 238000009863 impact test Methods 0.000 description 1
- 238000004519 manufacturing process Methods 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
- 239000013589 supplement Substances 0.000 description 1
Landscapes
- Heat Treatment Of Articles (AREA)
Abstract
Description
【発明の詳細な説明】
（産業上の利用分野）
この発明は、フラッシュバット溶接を施した引張り強さ
５０ｋｇｆ／ｍｍ２以上を有する高張力鋼の接合部にお
けるしん性の改善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 method for improving the toughness of a flash-butt welded high-tensile steel joint having a tensile strength of 50 kgf/mm2 or more.
（従来の技術）
フラッシュバット溶接は、高能率でしかも安定した溶接
部を得ることが可能であることからレール、ハイテンチ
ェーンあるいは鋼管環の溶接に広く利用されている。し
かし、フラッシュバット溶接を施した接合部や溶接熱影
否部（以下ＨＡＺと記す）に切り欠を付けた試料による
シャルピー試験においては、非常に低いエネルギーで破
断する不利があった。この原因としては、
１）フラッシュバット溶接時の脱炭および脱マンガンの
為に接合部がその周辺よりも軟化すること。(Prior Art) Flash butt welding is widely used for welding rails, high-tensile chains, and steel pipe rings because it is highly efficient and can produce stable welds. However, in the Charpy test using samples with flash-butt welded joints and samples with notches in the weld heat-affected area (hereinafter referred to as HAZ), they had the disadvantage of breaking at very low energy. The causes of this are: 1) The joint becomes softer than the surrounding area due to decarburization and demanganization during flash butt welding.
２）フラッシュバット溶接時の高温加熱により接合部の
オーステナイト結晶が粗大化すること。2) The austenite crystals in the joint become coarse due to high temperature heating during flash butt welding.
等が挙げられる。etc.
この点特公昭５６−２８９８６号公報では、フラッシュ
ハツト溶接による接合部のじん性の改善を図った低炭素
強じん鋼が提案されている。In this regard, Japanese Patent Publication No. 56-28986 proposes a low carbon strong steel in which the toughness of the joint is improved by flash hat welding.
（発明が解決しようとする問題点）
ところで上記公報に開示の技術では、溶接後の熱処理に
よって接合部の硬度が低下し接合部で破断するという問
題があり、フラッシュバット溶接を適用する場合に生じ
ていた不利を解消する効果的な手法が今だ開発されてい
ないのが現状であった。(Problems to be Solved by the Invention) However, with the technique disclosed in the above publication, there is a problem in that the hardness of the joint decreases due to heat treatment after welding, causing breakage at the joint, which occurs when flash butt welding is applied. The current situation is that no effective method has yet been developed to overcome these disadvantages.
この発明の目的は、フラッシュバット溶接を施した高張
力鋼のＨＡＺも含めた接合部において、じん性の改善を
図るのに有利な方法を提案するところにある。An object of the present invention is to propose an advantageous method for improving the toughness of flash-butt welded high-tensile steel joints, including HAZ.
（問題点を解決するための手段）
この発明は、Ｃ： ０．０２〜０．２０ｗｔχ （以下
単に％で示す） 、Ｓｔ ：０．１０〜０．８０％、Ｍ
ｎ ： １．００〜３．００％、Ａｌ ： ０．０１〜
０．０５％、Ｎｂ ： ０．０２〜０．１０％及びＶ：
０．０２〜０．１０％を含む組成になる高張力鋼にフラ
ッシュバット溶接を施したその接合部につき、９００℃
以上、１１００℃以下の温度域で加熱して１００〜１５
０秒間保持したのち、少なくとも８００〜５００℃の温
度域を５〜１５℃への冷却速度で冷却することを特徴と
するフラッシュバット溶接を施した高張力鋼の接合部の
じん性改善方法（第１発明）であり、またこの発明はＣ
： ０．０２〜０．２０％、Ｓｉ：０．１０〜０．８０
％、Ｍｎ ： １．００〜３．ＯＯ％、Ａｌ ： ０．
０１〜０．０５％、Ｎｂ ： ０．０２〜０．１０％お
よびＶ ： ０．０２〜０．１０％を含み、さらにＣｕ
： ０．１〜０．４％、Ｎｉ：０．１〜０．４％のな
かから選ばれるいずれか一種又は二種を含む組成になる
高張力鋼にフラッシュバット溶接を施したその接合部に
つき、９００ ’Ｃ以上、１１００℃以下の温度域に加
熱して１００〜１５０秒間保持したのち、少なくとも８
００〜ｓｏｏ ’ｃの温度域を５〜１５０℃／ｓの冷却
速度で冷却することを特徴とするフラッシュバット溶接
を施した高張力鋼の接合部のじん性改善方法（第２発明
）である。(Means for Solving the Problems) This invention provides C: 0.02 to 0.20wtχ (hereinafter simply expressed as %), St: 0.10 to 0.80%, M
n: 1.00~3.00%, Al: 0.01~
0.05%, Nb: 0.02-0.10% and V:
900℃ for flash-butt welded high-strength steel with a composition containing 0.02-0.10%
above, heated in a temperature range of 1100℃ or less to 100 to 15
A method for improving the toughness of a joint of high-strength steel subjected to flash butt welding, characterized by cooling at a cooling rate of at least 5 to 15 degrees Celsius in a temperature range of at least 800 to 500 degrees Celsius after holding for 0 seconds (Part 1) 1 invention), and this invention is C
: 0.02-0.20%, Si: 0.10-0.80
%, Mn: 1.00-3. OO%, Al: 0.
01-0.05%, Nb: 0.02-0.10% and V: 0.02-0.10%, further Cu
: 0.1 to 0.4%, Ni: 0.1 to 0.4%, and the joint part of high tensile steel with a composition containing one or two selected from 0.1 to 0.4%, flash butt welded. , after heating to a temperature range of 900'C or more and 1100°C or less and holding for 100 to 150 seconds, at least 8
A method for improving the toughness of a joint of high-strength steel subjected to flash butt welding (second invention), characterized by cooling in a temperature range of 00 to soo'c at a cooling rate of 5 to 150 °C/s. .
ここで上記高張力鋼における成分組成の限定理由につい
て説明する。Here, the reasons for limiting the composition of the high-strength steel will be explained.
まずＣについて、
Ｃはその含有率が０．０２％に満たないと鋼の強度が不
足し、また製造技術面におけるコストが非常に高くなる
。一方０．２０％を超えると接合部の結晶粒が粗大化す
るため焼きの入った組織になり、じん性劣化の原因とな
る。First, regarding C, if the content of C is less than 0.02%, the strength of the steel will be insufficient, and the cost in terms of manufacturing technology will be extremely high. On the other hand, if it exceeds 0.20%, the crystal grains in the joint become coarse, resulting in a hardened structure, which causes deterioration of toughness.
Ｍｎ ：
Ｍｎはフラッシュバット溶接中に脱マンガンによって焼
入性が不足しないように予め高めておく必要があり、そ
の含有率が１．００％に満たないと所望の強度を得るこ
とができず、一方３．００％を超えると硬くなりすぎ、
じん性が劣化する。Mn: Mn must be increased in advance to avoid insufficient hardenability due to demanganization during flash butt welding, and if its content is less than 1.00%, the desired strength cannot be obtained. On the other hand, if it exceeds 3.00%, it becomes too hard.
Toughness deteriorates.
Ｓｉ ：
ＳｉはＭｎ 、 ＡＩ とともに溶鋼の脱酸に欠ごとの
できない元素であり、その含有率が０．１０％未満では
脱酸の効果がなく、一方０．８０％超えて含有すると母
材のじん性が劣化する。Si: Along with Mn and AI, Si is an essential element for deoxidizing molten steel.If its content is less than 0.10%, there is no deoxidizing effect, while if it is contained in excess of 0.80%, it will damage the base metal. Toughness deteriorates.
Ａｌ ：
ＡＩは溶鋼の脱酸に少なくとも０．０１％以上必要であ
る。ところでＡＩの含有率が０．０５％を超えるとフラ
ッシュバット溶接中に＾１２０３が生成し母材のじん性
が劣化する。Al: Al is required to deoxidize molten steel in an amount of at least 0.01%. By the way, if the content of AI exceeds 0.05%, ^1203 will be generated during flash butt welding and the toughness of the base metal will deteriorate.
Ｎｂ 、 Ｖ ：
Ｎｂ、Ｖは溶鋼中のＣの活量を下げ、ワラシュバット溶
接時の脱炭を小さくし、またフラッシュバット溶接時の
アップセット過程における加圧、変形による高温加熱部
分の結晶粒を微細化して接合部のじん性を向上させるの
に重要な役割を果す元素であり、そのためにはそれぞれ
少なくとも０．０２％以上必要である。しかし０．１０
％を超えると却って母材を含めてじん性が劣化する。Nb, V: Nb and V reduce the activity of C in molten steel, reduce decarburization during flash butt welding, and reduce crystal grains in the high temperature heated part due to pressure and deformation during the upset process during flash butt welding. These are elements that play an important role in improving the toughness of joints through miniaturization, and for this purpose, each element is required in an amount of at least 0.02% or more. But 0.10
If it exceeds %, the toughness of the base material will actually deteriorate.
以上この発明に適合する高張力鋼の必須成分につき説明
したが、この他必要に応じてＣｕ 、 Ｎｉのうちから
選んだ少なくとも１種以上を含有させることができる。The essential components of high-strength steel suitable for the present invention have been described above, but in addition to these, at least one selected from Cu and Ni may be included as required.
Ｃｕは所望の強度を得るには０．１０％以上含有させる
のが望ましく、一方０．４０％超えると母材が硬くなり
すぎる。よってＣｕは０．１〜０．４％の範囲が好まし
い。In order to obtain the desired strength, it is desirable to contain Cu in an amount of 0.10% or more, while if it exceeds 0.40%, the base material becomes too hard. Therefore, Cu is preferably in a range of 0.1 to 0.4%.
Ｎｉ は母材のじん性を向上させるには最低０．１％含
有させるのが望ましく、低温じん性を考慮した場合でも
０．４％であれば充分な効果がある。In order to improve the toughness of the base metal, it is desirable to contain Ni at a minimum of 0.1%, and even when low-temperature toughness is taken into consideration, 0.4% has a sufficient effect.
なお鋼の強度を高めるため、必要に応じてＣｒを０．０
１〜０．０５％の範囲で添加してもよい。In order to increase the strength of the steel, Cr may be added to 0.0 if necessary.
It may be added in a range of 1 to 0.05%.
（作 用）
上記成分組成になる高張力鋼をフラッシュバット溶接し
た後に咳高張力鋼の接合部を９００〜１１００℃に加熱
するのは、接合部の脱元素（Ｃ，Ｍｎ）やオーステナイ
ト結晶粒の微細化に効果のあるＡＩ 。(Function) After flash-butt welding the high-strength steel with the above-mentioned composition, heating the joint of the high-strength steel to 900 to 1100°C will reduce elemental removal (C, Mn) and austenite crystal grains in the joint. AI is effective in miniaturizing.
ＮｂあるいはＶを母材からの拡散により、接合部及びＨ
ＡＺに補い、均一に分布させるためである。とくに加熱
温度が１１００℃を超えると接合部や）ＩＡＺだけでな
く母材の結晶粒も粗大化しじん性を劣化させる。By diffusing Nb or V from the base material, the joints and H
This is to supplement AZ and distribute it uniformly. In particular, when the heating temperature exceeds 1100° C., not only the joint portion and IAZ but also the crystal grains of the base material become coarse and the toughness deteriorates.
次に上記の温度域において１００〜１５０秒間保持する
のは、処理対称物の板厚や径によっても異なるが、１０
０秒よりも短いと接合部付近は充分再結晶させることが
、できずじん性はＭＳ−Ｗｅｌｄ時と変らない。一方１
５０秒を超えると再結晶粒が粗大化しじん性が劣化する
からである。Next, holding the temperature in the above temperature range for 100 to 150 seconds varies depending on the thickness and diameter of the object to be processed, but
If it is shorter than 0 seconds, the vicinity of the joint cannot be sufficiently recrystallized, and the toughness remains the same as in MS-Weld. On the other hand 1
This is because if the time exceeds 50 seconds, the recrystallized grains will become coarse and the toughness will deteriorate.
次にＥＩＡＺを含めた接合部の冷却に際して少なくとも
８００〜５００℃の温度域を５〜１５０℃／ｓの冷却速
度で冷却するのは、冷却速度が５℃／Ｓに満たないと微
細化した結晶粒が成長し、一方１５０℃／ｓを超えると
焼き入った硬化組織となり、却って接合部およびＨＡＺ
のじん性が劣化するからである。Next, when cooling the joint including EIAZ, it is important to cool the temperature range of at least 800 to 500°C at a cooling rate of 5 to 150°C/s.If the cooling rate is less than 5°C/s, fine crystals On the other hand, if the temperature exceeds 150°C/s, the grains will grow and become a hardened structure, which will actually cause the joints and HAZ to grow.
This is because the toughness deteriorates.
なお、上述した熱処理は、とくにフラッシュバット溶接
を施した対象物の接合部中心から２０ｍｍ〜２００ ｍ
ｍの範囲において実施するのが好ましい。In addition, the above-mentioned heat treatment is performed especially at a distance of 20 mm to 200 m from the center of the joint of the object subjected to flash butt welding.
It is preferable to carry out in the range of m.
この発明において、高張力鋼にフラッシュバット溶接を
施した際、上記の如き処理によりＨＡＺを含めた接合部
のじん性を改善できる理由としては■フラッシュバット
溶接時の高温加熱により粗大化したオーステナイト結晶
粒を溶接後冷却し、最適再結晶温度域で加熱保持し、適
度な冷却速度で冷却することで接合部及びＨＡＺを微細
な再結晶とすることができ、又、この加熱保持の時、母
材からのＡＩ 、 Ｎｂ 、 Ｖの拡散もオーステナイ
ト結晶粒の微細化を促進させる。In this invention, when performing flash butt welding on high tensile strength steel, the reasons why the toughness of the joint including the HAZ can be improved by the above treatment are as follows. By cooling the grains after welding, keeping them heated in the optimum recrystallization temperature range, and cooling them at an appropriate cooling rate, it is possible to make the joint and HAZ finely recrystallized. Diffusion of AI, Nb, and V from the material also promotes refinement of austenite grains.
■さらに、母材からのＣ、Ｍｎの拡散により、溶接時に
おけるＣ１Ｍｎの不足量を補ない、接合部の軟化を防止
する作用があるため、
と考えられる。■Furthermore, it is thought that the diffusion of C and Mn from the base metal compensates for the lack of C1Mn during welding and prevents the joint from softening.
（実施例）
第１表に示す化学成分になる高張力鋼板（厚さ１８ｍｍ
Ｘ幅１００朋×長さ５００鴫）を用意して、下記の条件
にてフラッシュバット溶接を行い、その後常温まで冷却
（放冷）した。(Example) High-strength steel plate (18 mm thick) with the chemical composition shown in Table 1
Flash butt welding was performed under the conditions described below, and then cooled to room temperature (left to cool).
溶接条件：溶接電圧 １０Ｖ
フラッシュ代 ２５ｍｍ
アップセット力 ２０トン
次に溶接部における余盛り部をグラインダーにて除去し
、板厚の中心からＪＩＳ規格に基づいたシャルピー試験
用の試験片を切り出し、第２表に示す条件で熱処理した
のち、接合部およびＨＡＺにおける衝撃試験を行った。Welding conditions: Welding voltage: 10V Flash distance: 25mm Upset force: 20 tons Next, the excess portion of the welded part was removed using a grinder, and a test piece for the Charpy test based on the JIS standard was cut from the center of the plate thickness. After heat treatment under the conditions shown in the table, an impact test was conducted at the joint and HAZ.
その結果を第２表に併せて示す。The results are also shown in Table 2.
第２表
なお第２表中の熱処理後の冷却は、Ａｒガスを用い、そ
の流量調整により冷却速度を変化させた。Table 2 Note that Ar gas was used for cooling after the heat treatment in Table 2, and the cooling rate was varied by adjusting the flow rate.
第２表より明らかなようにこの発明に適合する鋼とは異
なる成分の鋼Ｇ、）１． （試験片Ｎｏ、７．８）を用
いてフラッシュバット溶接を行い、前述した要領で熱処
理しても接合部及びＨＡＺの吸収エネルギーはせいぜい
１．０〜４．Ｏｋｇｆｍを示すのみであった。As is clear from Table 2, steel G whose composition is different from that of the steel conforming to the present invention)1. Even if flash butt welding is performed using (test piece No. 7.8) and heat treatment is performed as described above, the absorbed energy of the joint and HAZ is at most 1.0 to 4. It only showed Okgfm.
また、この発明に適合する鋼のうちとくにＡ、 Ｃに
つき、この発明とは異なる条件にて熱処理した°もの（
試験片Ｎｏ、９．１．８）は、やはり顕著な改善は見ら
れなかった。In addition, among the steels compatible with this invention, steels A and C in particular are heat-treated under conditions different from those of this invention (
As for test piece No. 9.1.8), no significant improvement was observed.
この発明に従うものについては接合部において７〜１０
ｋｇｆｍ、 ＨＡＺにおいて７〜１２ｋｇｆｍを示しじ
ん性の顕著な改善が確かめられた。7 to 10 at the joint for those according to this invention.
kgfm, HAZ showed 7 to 12 kgfm, confirming a remarkable improvement in toughness.
第２表中の試験片Ｎｏ、 ３の接合部における組織写真
を第１図（ａ）（ｂ）に示す。第１図（ａ）は、ＡＳ−
Ｗｅｌｄでの組織を示すもので、フラッシュバット溶接
により、粗大オーステナイト粒となりその粒内でベイナ
イト組織がみられる。第１図（ｂ）はこの発明に従う要
領にて熱処理を施したのであり、再結晶の微細化効果に
より細かい組織となっている。Photographs of the structure at the joint of test specimen No. 3 in Table 2 are shown in FIGS. 1(a) and 1(b). FIG. 1(a) shows AS-
This shows the structure during welding, and flash butt welding results in coarse austenite grains and a bainite structure can be seen within the grains. In FIG. 1(b), heat treatment was performed according to the method according to the present invention, and a fine structure was obtained due to the refinement effect of recrystallization.
また第２図に試験片Ｎα４及び７における接合部付近の
硬さ分布を示す。図においてＮｏ、 ４は接合部に軟化
は見られず、均一な硬さ分布であることがわかるが、Ｎ
ｏ、 ７では接合部が軟化していることがわかる。Further, FIG. 2 shows the hardness distribution near the joint in test pieces Nα4 and Nα7. In the figure, No. 4 shows no softening in the joint and has a uniform hardness distribution, but No.
It can be seen that the joints in samples o and 7 are softened.
（発明の効果）
この発明によれば、フラッシュバット溶接による高張力
鋼の接合部やＨＡＺのじん性を有利に改善することがで
きる。(Effects of the Invention) According to the present invention, it is possible to advantageously improve the toughness of high-tensile steel joints and HAZ by flash butt welding.
第１図（ａ）、 （ｂ）は、実施例における試験片の金
属組織写真、
第２図は、実施例における試験片の硬さ分布を示すグラ
フである。
第１図
（ａ）
（ｂｙ
候がｔ ｔ （Ｘ４００）FIGS. 1(a) and 1(b) are photographs of the metallographic structure of the test pieces in Examples, and FIG. 2 is a graph showing the hardness distribution of the test pieces in Examples. Figure 1 (a) (by t t (X400)
Claims (1)
１００℃以下の温度域に加熱して１００〜１５０秒間保
持したのち、少なくとも８００〜５００℃の温度域を５
〜１５０℃／ｓの冷却速度で冷却することを特徴とする
フラッシュバット溶接を施した高張力鋼の接合部のじん
性改善方法。 ２、Ｃ：０．０２〜０．２０ｗｔ％、 Ｓｉ：０．１０〜０．８０ｗｔ％、 Ｍｎ：１．００〜３．００ｗｔ％、 Ａｌ：０．０１〜０．０５ｗｔ％、 Ｎｂ：０．０２〜０．１０ｗｔ％および Ｖ：０．０２〜０．１０ｗｔ％を含み、 さらにＣｕ：０．１〜０．４ｗｔ％、Ｎｉ：０．１〜０
．４ｗｔ％のなかから選ばれるいずれか一種又は二種を
含む組成になる高張力鋼にフラッシュバット溶接を施し
たその接合部につき、９００℃以上、１１００℃以下の
温度域に加熱して１００〜１５０秒間保持したのち、少
なくとも８００〜５００℃の温度域を５〜１５℃／ｓの
冷却速度で冷却することを特徴とするフラッシュバット
溶接を施した高張力鋼の接合部のじん性改善方法。[Claims] 1. C: 0.02 to 0.20 wt%, Si: 0.10 to 0.80 wt%, Mn: 1.00 to 3.00 wt%, Al: 0.01 to 0.05 wt%. %, Nb: 0.02 to 0.10 wt%, and V: 0.02 to 0.10 wt%.
After heating to a temperature range of 100°C or less and holding for 100 to 150 seconds, heat to a temperature range of at least 800 to 500°C for 5
A method for improving the toughness of a joint of high-strength steel subjected to flash butt welding, characterized by cooling at a cooling rate of ~150°C/s. 2, C: 0.02 to 0.20 wt%, Si: 0.10 to 0.80 wt%, Mn: 1.00 to 3.00 wt%, Al: 0.01 to 0.05 wt%, Nb: 0. 02-0.10 wt% and V: 0.02-0.10 wt%, further Cu: 0.1-0.4 wt%, Ni: 0.1-0
．． 4wt% of high-tensile steel with a composition containing one or two selected from among them, flash butt welded and heated to a temperature range of 900°C or higher and 1100°C or lower to 100-150°C. 1. A method for improving the toughness of a joint of high-strength steel subjected to flash butt welding, which comprises holding the joint for a second and then cooling the joint in a temperature range of at least 800 to 500°C at a cooling rate of 5 to 15°C/s.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP24814887A JPH0192320A (en) | 1987-10-02 | 1987-10-02 | Improvement of toughness of joint of high tension steel subjected to flash butt welding |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP24814887A JPH0192320A (en) | 1987-10-02 | 1987-10-02 | Improvement of toughness of joint of high tension steel subjected to flash butt welding |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH0192320A true JPH0192320A (en) | 1989-04-11 |
Family
ID=17173932
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP24814887A Pending JPH0192320A (en) | 1987-10-02 | 1987-10-02 | Improvement of toughness of joint of high tension steel subjected to flash butt welding |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH0192320A (en) |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2001007667A1 (en) * | 1999-07-27 | 2001-02-01 | The Timken Company | Method of improving the toughness of low-carbon, high-strength steels |
| CN105132801A (en) * | 2015-08-07 | 2015-12-09 | 舞阳钢铁有限责任公司 | Engineering mechanical steel plate with high surface quality requirement and production method for engineering mechanical steel plate |
| EP3292889A1 (en) | 2009-01-19 | 2018-03-14 | Hochiki Corporation | Electrification spray head |
-
1987
- 1987-10-02 JP JP24814887A patent/JPH0192320A/en active Pending
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2001007667A1 (en) * | 1999-07-27 | 2001-02-01 | The Timken Company | Method of improving the toughness of low-carbon, high-strength steels |
| EP3292889A1 (en) | 2009-01-19 | 2018-03-14 | Hochiki Corporation | Electrification spray head |
| CN105132801A (en) * | 2015-08-07 | 2015-12-09 | 舞阳钢铁有限责任公司 | Engineering mechanical steel plate with high surface quality requirement and production method for engineering mechanical steel plate |
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