JP6319217B2 - Steel plate welding method and steel plate welding apparatus - Google Patents
Steel plate welding method and steel plate welding apparatus Download PDFInfo
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- JP6319217B2 JP6319217B2 JP2015147609A JP2015147609A JP6319217B2 JP 6319217 B2 JP6319217 B2 JP 6319217B2 JP 2015147609 A JP2015147609 A JP 2015147609A JP 2015147609 A JP2015147609 A JP 2015147609A JP 6319217 B2 JP6319217 B2 JP 6319217B2
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- 229910000831 Steel Inorganic materials 0.000 title claims description 97
- 239000010959 steel Substances 0.000 title claims description 97
- 238000003466 welding Methods 0.000 title claims description 76
- 238000000034 method Methods 0.000 title claims description 41
- 238000005096 rolling process Methods 0.000 claims description 45
- 238000005097 cold rolling Methods 0.000 claims description 27
- 239000010960 cold rolled steel Substances 0.000 claims 1
- 239000007789 gas Substances 0.000 description 33
- 239000002184 metal Substances 0.000 description 13
- 239000000463 material Substances 0.000 description 6
- 239000011261 inert gas Substances 0.000 description 5
- 238000010586 diagram Methods 0.000 description 3
- 239000010953 base metal Substances 0.000 description 2
- 239000000945 filler Substances 0.000 description 2
- 230000003647 oxidation Effects 0.000 description 2
- 238000007254 oxidation reaction Methods 0.000 description 2
- 230000002159 abnormal effect Effects 0.000 description 1
- 238000000137 annealing Methods 0.000 description 1
- 239000012141 concentrate Substances 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 230000007423 decrease Effects 0.000 description 1
- 238000007865 diluting Methods 0.000 description 1
- 238000005098 hot rolling Methods 0.000 description 1
- 238000005554 pickling Methods 0.000 description 1
- 239000007921 spray Substances 0.000 description 1
- 229910001220 stainless steel Inorganic materials 0.000 description 1
- 239000010935 stainless steel Substances 0.000 description 1
- 229910000859 α-Fe Inorganic materials 0.000 description 1
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Description
本発明は、鋼板の連続冷間圧延ラインにおいて、冷間圧延を行う前に先行材と後行材とを溶接する鋼板の溶接方法および鋼板の溶接装置に関する。 The present invention relates to a steel plate welding method and a steel plate welding apparatus for welding a preceding material and a succeeding material before performing cold rolling in a continuous cold rolling line for steel plates.
一般に、鋼板を製造するプロセスラインは、熱間圧延、酸洗、冷間圧延、焼鈍が連続した連続ラインの形態が主流となっている。このような鋼板の連続ラインでは、処理対象の鋼板を間断なく供給するために、連続ラインの入側で先行材と後行材とを突合せ溶接により接合している。このような鋼板同士の溶接は、フラッシュバット溶接やレーザー溶接による場合が多い。特に電磁鋼板やステンレス鋼板などの難圧延材について、冷間圧延を行う連続ライン（連続冷間圧延ライン）では、多くの場合、レーザー溶接によって溶接される。 In general, a process line for producing a steel sheet is mainly in the form of a continuous line in which hot rolling, pickling, cold rolling, and annealing are continuous. In such a continuous line of steel plates, in order to supply the steel plate to be processed without interruption, the preceding material and the following material are joined by butt welding on the entry side of the continuous line. Such welding between steel plates is often performed by flash butt welding or laser welding. In particular, with regard to difficult-to-roll materials such as electromagnetic steel plates and stainless steel plates, a continuous line (continuous cold rolling line) for cold rolling is often welded by laser welding.
レーザー溶接では、非特許文献１に記載されているように、発振器で生成されたレーザー光が導光路を介して集光レンズで集光された後、鋼板間に供給された溶接金属に照射される。溶接金属は、照射されたレーザー光を熱源として加熱され溶融し、溶接部を形成する。その際、溶融した溶接金属の酸化を防止するため、ＡｒやＨｅ等の不活性ガスがアシストガスとして供給される。 In laser welding, as described in Non-Patent Document 1, laser light generated by an oscillator is condensed by a condenser lens through a light guide and then irradiated to a weld metal supplied between steel plates. The The weld metal is heated and melted using the irradiated laser beam as a heat source to form a weld. At that time, an inert gas such as Ar or He is supplied as an assist gas in order to prevent oxidation of the molten weld metal.
しかしながら、連続冷間圧延ラインでは、鋼板がレーザー溶接後に急冷されて硬化するため、溶接部の靱性が十分に確保されない。特に、Ｓｉを多く含む電磁鋼板に対して連続冷間圧延ラインでレーザー溶接が行われた場合、溶接部は著しく脆化し、冷間圧延時に破断する場合がある。鋼中のＳｉ含有量が多いほど、その傾向は著しい。冷間圧延中に鋼板が破断すると、復旧に時間がかかり、連続冷間圧延ラインの稼働率が低下してしまう。また、圧延ロールがダメージを受けることにより圧延ロール原単位が悪化してしまう。 However, in the continuous cold rolling line, the steel sheet is quenched and hardened after laser welding, so that the toughness of the welded portion is not sufficiently ensured. In particular, when laser welding is performed on a magnetic steel sheet containing a large amount of Si in a continuous cold rolling line, the welded portion may become significantly brittle and may break during cold rolling. The tendency is remarkable, so that there is much Si content in steel. If the steel sheet breaks during cold rolling, it takes time to recover, and the operating rate of the continuous cold rolling line decreases. Moreover, when a rolling roll receives damage, a rolling roll basic unit will deteriorate.
そこで、特許文献１には、電磁鋼板を溶接する際に、フィラーを添加して溶接金属のＳｉを希釈することにより、靱性に優れた溶接継手（溶接部）を得る技術が記載されている。この技術により、電磁鋼板を溶接する際に、溶接部に粗大フェライトが生成され機械的性質が劣化することや、熱影響部で結晶粒が粗大化して熱影響部で破断することを防止している。 Therefore, Patent Document 1 describes a technique for obtaining a welded joint (welded portion) having excellent toughness by adding filler and diluting Si of a weld metal when welding an electromagnetic steel sheet. With this technology, when welding magnetic steel sheets, coarse ferrite is generated in the welded part and mechanical properties are deteriorated, and crystal grains are coarsened in the heat-affected zone and fractured in the heat-affected zone. Yes.
しかしながら、Ｓｉ含有量が１．０重量％以上の電磁鋼板では、レーザー溶接時にフィラーを添加して溶接部のＳｉを希釈しても、冷間圧延中の鋼板の破断を完全に防止することはできないという問題があった。 However, in an electromagnetic steel sheet having a Si content of 1.0% by weight or more, even if a filler is added during laser welding to dilute Si in the weld, it is possible to completely prevent the steel sheet from being broken during cold rolling. There was a problem that I could not.
本発明は、上記に鑑みてなされたものであって、冷間圧延中に溶接部で破断が発生しない鋼板の溶接方法および鋼板の溶接装置を提供することを目的とする。 This invention is made | formed in view of the above, Comprising: It aims at providing the welding method of the steel plate which does not generate | occur | produce a fracture | rupture in a welding part during cold rolling, and the welding apparatus of a steel plate.
上述した課題を解決し、目的を達成するために、本発明に係る鋼板の溶接方法は、冷間圧延処理に先だって、連続して該冷間圧延処理の対象となる２枚の鋼板の端部同士を溶接する鋼板の溶接方法であって、前記鋼板のおもて面に噴射する、レーザー溶接のアシストガスの種類および／または流量と、前記鋼板の裏面に噴射する、レーザー溶接のアシストガスの種類および／または流量とを、互いに異なるように調整して、前記端部間に形成される溶接部を、前記鋼板のおもて面からの突出量と裏面からの突出量とが均等な形状、かつ前記鋼板のおもて面における圧延方向長さと裏面における圧延方向長さとが均等な形状に突出させるよう制御する形状制御ステップを含み、前記溶接部を突出させた状態で前記鋼板が冷間圧延されることを特徴とする。 In order to solve the above-described problems and achieve the object, the steel sheet welding method according to the present invention is the end of two steel sheets that are successively subjected to the cold rolling process prior to the cold rolling process. A method of welding steel plates that welds each other, the type and / or flow rate of laser welding assist gas that is injected onto the front surface of the steel plate, and laser welding assist gas that is injected onto the back surface of the steel plate. The type and / or flow rate are adjusted to be different from each other, and the weld formed between the end portions is shaped so that the amount of protrusion from the front surface of the steel plate and the amount of protrusion from the back surface are equal. and viewed including the shape control step of controlling so as to project in the rolling direction length and are uniform shape in the rolling direction length and the back of the front surface of the steel sheet, the steel sheet is cooled at a state of being projected the weld Japanese to be between rolled To.
また、本発明に係る鋼板の溶接装置は、冷間圧延処理に先だって、連続して該冷間圧延処理の対象となる２枚の鋼板の端部同士を溶接する鋼板の溶接装置であって、前記鋼板のおもて面に噴射する、レーザー溶接のアシストガスの種類および／または流量と、前記鋼板の裏面に噴射する、レーザー溶接のアシストガスの種類および／または流量とを、互いに異なるように調整して、前記端部間に形成される溶接部を、前記鋼板のおもて面からの突出量と裏面からの突出量とが均等な形状、かつ前記鋼板のおもて面における圧延方向長さと裏面における圧延方向長さとが均等な形状に突出させるよう制御する形状制御手段を備え、前記溶接部を突出させた状態で前記鋼板が冷間圧延されるよう配置されていることを特徴とする。 In addition, the steel sheet welding apparatus according to the present invention is a steel sheet welding apparatus that welds the ends of two steel sheets that are the targets of the cold rolling process continuously before the cold rolling process, The type and / or flow rate of the assist gas for laser welding injected onto the front surface of the steel plate and the type and / or flow rate of the assist gas for laser welding injected onto the back surface of the steel plate are different from each other. The welded portion formed between the end portions is adjusted so that the protruding amount from the front surface of the steel plate and the protruding amount from the back surface are uniform, and the rolling direction on the front surface of the steel plate with a shape control means and the rolling direction length in length and the rear surface is controlled so as to protrude into equal shape, the steel sheet in a state of being projected the weld and features that you have been arranged to be cold rolled To do.
本発明によれば、冷間圧延中に溶接部で破断が発生することを防止することができる。 According to the present invention, it is possible to prevent a fracture from occurring at a weld during cold rolling.
以下、図面を参照して、本発明の一実施形態である溶接装置および溶接処理を詳細に説明する。なお、この実施の形態により本発明が限定されるものではない。また、図面の記載において、同一部分には同一の符号を付して示している。 Hereinafter, a welding apparatus and a welding process according to an embodiment of the present invention will be described in detail with reference to the drawings. In addition, this invention is not limited by this embodiment. Moreover, in description of drawing, the same code | symbol is attached | subjected and shown to the same part.
［発明の原理］
まず、図１〜４を参照して、本発明の原理について説明する。従来、連続冷間圧延ライン上を前後して搬送される２枚の鋼鈑Ｓをレーザー溶接により溶接すると、鋼板Ｓ間に形成される溶接部Ｍは、鋼板Ｓのおもて面からの突出量と裏面からの突出量とが不均等な形状になる。この場合、図１に例示するように、溶接部Ｍの圧延方向Ａおよび圧下方向Ｂに平行な断面形状において、鋼板Ｓのおもて面からの突出量ｅ１と裏面からの突出量ｅ２（図１において、ｅ２≒０のため不図示）とが不均等になる。
[Principle of the Invention]
First, the principle of the present invention will be described with reference to FIGS. Conventionally, when two steel sheets S conveyed back and forth on a continuous cold rolling line are welded by laser welding, the welded portion M formed between the steel sheets S protrudes from the front surface of the steel sheet S. The amount and the amount of protrusion from the back surface are uneven. In this case, as illustrated in FIG. 1, in the cross-sectional shape parallel to the rolling direction A and the reduction direction B of the weld M, the protrusion amount e1 from the front surface of the steel sheet S and the protrusion amount e2 from the back surface (FIG. 1 is not equal to e2≈0 (not shown).
この溶接部Ｍに対して冷間圧延処理を行うと、図２に例示するように、圧延された溶接部Ｍの圧延方向Ａおよび圧下方向Ｂに平行な断面形状は、鋼板Ｓの板厚の中心線Ｃを対称軸として非対称の形状になる。すなわち、図２に楕円で囲んで示す領域Ｒ１のように、同一の圧下方向Ｂ線上で、溶接部Ｍの溶接金属が鋼板Ｓのおもて面あるいは裏面のいずれか一方にのみに表出する領域が生じる。このような領域Ｒ１では、鋼板Ｓのおもて面と裏面とで延性が異なることにより、圧延時に鋼板Ｓの母材と溶接部Ｍの溶接金属との境界部分に歪が集中して破断の起点となってしまう。 When the cold rolling process is performed on the weld M, the cross-sectional shape parallel to the rolling direction A and the rolling direction B of the rolled weld M is the thickness of the steel sheet S as illustrated in FIG. It becomes an asymmetrical shape with the center line C as an axis of symmetry. That is, the weld metal of the welded portion M appears only on either the front surface or the back surface of the steel sheet S on the same rolling direction B line, as in a region R1 surrounded by an ellipse in FIG. An area arises. In such a region R1, since the ductility differs between the front surface and the back surface of the steel sheet S, strain concentrates on the boundary portion between the base metal of the steel sheet S and the weld metal of the weld M during rolling, and the fracture occurs. It becomes the starting point.
一方、溶接部Ｍが、鋼板Ｓのおもて面からの突出量と裏面からの突出量とが均等な形状であれば、図３に例示するように、溶接部Ｍの圧延方向Ａおよび圧下方向Ｂに平行な断面形状は、鋼板Ｓのおもて面からの突出量ｅ１と裏面からの突出量ｅ２とが均等になる。この場合、図４に例示するように、圧延された溶接部Ｍの圧延方向Ａおよび圧下方向Ｂに平行な断面形状は、鋼板Ｓの板厚の中心線Ｃを対称軸としてほぼ線対称の形状になる。すなわち、図４に丸で囲んで示す領域Ｒ２のように、溶接部Ｍの溶接金属は、同一の圧下方向Ｂ線上で鋼板Ｓのおもて面および裏面の両面に表出する。このような領域Ｒ２では、鋼板Ｓの両面の延性が同じであるため、鋼板Ｓに歪が生じることがなく破断が発生しない。 On the other hand, if the welding part M has a shape in which the amount of protrusion from the front surface of the steel sheet S and the amount of protrusion from the back surface are uniform, as illustrated in FIG. In the cross-sectional shape parallel to the direction B, the protruding amount e1 from the front surface of the steel sheet S and the protruding amount e2 from the back surface are equal. In this case, as illustrated in FIG. 4, the cross-sectional shape of the rolled weld M that is parallel to the rolling direction A and the rolling direction B is a substantially line-symmetric shape with the center line C of the thickness of the steel sheet S as the symmetry axis. become. That is, as shown in a region R2 circled in FIG. 4, the weld metal of the welded portion M appears on both the front surface and the back surface of the steel sheet S on the same rolling direction B line. In such area | region R2, since the ductility of both surfaces of the steel plate S is the same, a distortion does not arise in the steel plate S and a fracture | rupture does not generate | occur | produce.
本発明は、溶接部Ｍの形状を、鋼板Ｓのおもて面からの突出量と裏面からの突出量とが均等な形状に制御するものである。ここで、鋼板Ｓのおもて面からの突出量と裏面からの突出量とが均等とは、溶接部Ｍの圧延方向Ａおよび圧下方向Ｂに平行な断面において、母材に対する溶接金属の板厚方向のおもて面からの突出量ｅ１と裏面からの突出量ｅ２との差が２０％以内の範囲であることを意味する。また、鋼板Ｓのおもて面および裏面からの突出量とは、溶接される２枚の鋼板Ｓの板厚が異なる場合には、先行材のおもて面および裏面からの突出量を意味する。 In the present invention, the shape of the welded portion M is controlled so that the protruding amount from the front surface of the steel sheet S and the protruding amount from the back surface are equal. Here, the amount of protrusion from the front surface of the steel sheet S and the amount of protrusion from the back surface are equal to each other in the cross section parallel to the rolling direction A and the rolling direction B of the welded part M. It means that the difference between the protruding amount e1 from the front surface in the thickness direction and the protruding amount e2 from the back surface is within 20%. Further, the protruding amount from the front surface and the back surface of the steel sheet S means the protruding amount from the front surface and the back surface of the preceding material when the thicknesses of the two steel plates S to be welded are different. To do.
また、図１では、溶接部Ｍの圧延方向Ａおよび圧下方向Ｂに平行な断面において、鋼板Ｓのおもて面における溶接部Ｍの圧延方向長さｆ１と裏面における溶接部Ｍの圧延方向長さｆ２とが不均等となっている。これらの溶接部Ｍの圧延方向長さの不均等は、溶接部Ｍの突出量の不均等に比べて圧延された溶接部Ｍの断面形状に与える影響は少ないが、圧延前の溶接部Ｍの圧延方向長さをより均等とすることによって、圧延された溶接部Ｍの断面形状を、鋼板Ｓの板厚の中心線Ｃを対称軸としてより線対称に近い形状とすることができる。よって、本発明では、さらに溶接部Ｍの形状を、鋼板Ｓのおもて面における溶接部Ｍの圧延方向長さｆ１と裏面における溶接部Ｍの圧延方向長さｆ２とが均等である形状に制御することが好ましい。ここで、鋼板Ｓのおもて面における溶接部Ｍの圧延方向長さｆ１と裏面における溶接部Ｍの圧延方向長さｆ２とが均等であるとは、溶接部Ｍの圧延方向Ａおよび圧下方向Ｂに平行な断面において、母材に対する溶接金属のおもて面における圧延方向長さｆ１と裏面における圧延方向長さｆ２との差の絶対値が圧延方向長さｆ１又は圧延方向長さｆ２のいずれか長い方に対して２０％以下の範囲内にあることを意味する。 Moreover, in FIG. 1, in the cross section parallel to the rolling direction A and the reduction direction B of the welded part M, the rolling direction length f1 of the welded part M on the front surface of the steel sheet S and the rolled direction length of the welded part M on the back surface. F2 is unequal. The unevenness in the length in the rolling direction of these welds M has less influence on the cross-sectional shape of the welded part M that is rolled compared to the unevenness in the protruding amount of the welds M. By making the length in the rolling direction more uniform, the cross-sectional shape of the rolled welded part M can be made closer to line symmetry with the center line C of the plate thickness of the steel sheet S as the symmetry axis. Therefore, in this invention, the shape of the welding part M is further made into the shape where the rolling direction length f1 of the welding part M in the front surface of the steel plate S and the rolling direction length f2 of the welding part M in the back surface are equal. It is preferable to control. Here, the rolling direction length f1 of the welded part M on the front surface of the steel sheet S and the rolling direction length f2 of the welded part M on the back surface are equal to each other. In the cross section parallel to B, the absolute value of the difference between the rolling direction length f1 on the front surface of the weld metal relative to the base metal and the rolling direction length f2 on the back surface is the rolling direction length f1 or the rolling direction length f2. It means that it is in the range of 20% or less for the longer one.
［溶接装置の構成］
次に、図５を参照して、本実施の形態の溶接装置について説明する。図５に示すように、溶接装置１は、発振器２、導光路３、集光部４、ワイヤー供給装置５および制御部６を備えて構成される。制御部６は、処理プログラムを実行するＣＰＵ等の演算処理装置を用いて実現され、溶接装置１の各構成部を制御する。
[Configuration of welding equipment]
Next, with reference to FIG. 5, the welding apparatus of this Embodiment is demonstrated. As shown in FIG. 5, the welding apparatus 1 includes an
この制御部６の制御により、発振器２で生成されたレーザー光Ｌは、導光路３を介して集光部４の集光レンズで集光され、溶接部Ｍに照射される。この溶接部Ｍは、接合する２枚の鋼板Ｓの端部間に、ワイヤー供給装置５から供給された溶接金属で構成される。溶接部Ｍの溶接金属が、照射されたレーザー光Ｌにより加熱され溶融することにより、２枚の鋼板Ｓの端部同士が接合される。
Under the control of the
この溶接装置１において、溶融した金属の酸化や溶接過程でのプラズマの発生を防止するために、ＡｒやＨｅ等の不活性ガスからなるアシストガスが供給される。アシストガスは、レーザー光Ｌによる溶接特性を左右する重要なパラメータの一つである。本実施の形態の溶接装置１では、アシストガスとして、センターガスＧ１と、サイドガスＧ２と、バックガスＧ３とが、制御部６の制御により噴射される。センターガスＧ１は、レーザー光Ｌと同軸に鋼板Ｓのおもて面に噴射される。サイドガスＧ２は、鋼板Ｓのおもて面にサイドから噴射される。バックガスＧ３は、鋼板Ｓの裏面に噴射される。
In this welding apparatus 1, an assist gas made of an inert gas such as Ar or He is supplied in order to prevent oxidation of molten metal or generation of plasma during the welding process. The assist gas is one of important parameters that affect the welding characteristics of the laser beam L. In the welding apparatus 1 of the present embodiment, the center gas G1, the side gas G2, and the back gas G3 are injected as the assist gas under the control of the
［溶接処理］
本実施の形態の溶接処理では、制御部６が、アシストガスの種類および流量を制御することにより、溶接部Ｍの形状を制御する形状制御処理を行う。具体的に、制御部６は、鋼板Ｓのおもて面に噴射するアシストガスの種類および流量と、裏面に噴射するアシストガスの種類および流量とを互いに異なるものに調整する。本実施例では、制御部６は、センターガスＧ１およびサイドガスＧ２により、鋼板Ｓのおもて面に所定の流量の不活性ガスを噴射させる。また、制御部６は、バックガスＧ３により、鋼板Ｓの裏面に、おもて面とは異なった所定の流量で不活性ガスを噴射させる、もしくはおもて面とは異なる種類の不活性ガスを噴射させる。これにより、溶接部Ｍの形状は、図３に例示するように、鋼板Ｓのおもて面からの突出量ｅ１と裏面からの突出量ｅ２とが均等な形状となり、あるいはさらに鋼板Ｓのおもて面における圧延方向長さｆ１と裏面における圧延方向長さｆ２とが均等な形状となる。
[Welding process]
In the welding process of the present embodiment, the
なお、鋼板Ｓのおもて面に噴射するアシストガスと裏面に噴射するアシストガスとは、種類あるいは流量のいずれか一方が異なればよい。 It should be noted that the assist gas injected to the front surface of the steel sheet S and the assist gas injected to the back surface may be different in either type or flow rate.
また、これらのアシストガスに加え、溶融した溶接金属と空気との接触を遮断するシールドガスを使って、溶接部Ｍの形状を制御してもよい。 Further, in addition to these assist gases, the shape of the welded portion M may be controlled using a shield gas that blocks contact between the molten weld metal and air.
以上、説明したように、本実施の形態の溶接装置および溶接処理によれば、制御部６が鋼板Ｓのおもて面に噴射するアシストガスの種類および／または流量と、鋼板Ｓの裏面に噴射するアシストガスの種類および／または流量とを、互いに異なるように調整することにより、溶接部Ｍの形状を、鋼板Ｓのおもて面からの突出量ｅ１と裏面からの突出量ｅ２とが均等な形状に制御する。これにより、圧延後の溶接部Ｍにおいて、同一の圧下方向Ｂ線上で、溶接金属が鋼板Ｓのおもて面および裏面の両面に表出し、両面の延性が同じになる。そのため、鋼板Ｓに局所的な歪が生じて異常変形が起こることが抑制されて破断の発生が防止され、生産性が高く安定した冷間圧延を行うことが可能となる。
As described above, according to the welding apparatus and the welding process of the present embodiment, the type and / or flow rate of the assist gas that the
［実施例］
板厚が０．４０ｍｍ〜３．５ｍｍの範囲の電磁鋼板を対象に、連続冷間圧延ラインに従来の溶接処理と本発明の溶接処理とを適用した。
[Example]
The conventional welding process and the welding process of the present invention were applied to a continuous cold rolling line for a magnetic steel sheet having a thickness of 0.40 mm to 3.5 mm.
本発明の溶接処理として、鋼板Ｓのおもて面に一定量のＡｒガスを噴射し、鋼板Ｓの裏面に、おもて面より少ない流量に種々調整したＡｒガスを噴射し、溶接部Ｍの形状を制御した。これにより、溶接部Ｍの形状は、鋼板Ｓのおもて面からの突出量ｅ１と裏面からの突出量ｅ２とが均等な形状になった（本発明１）。この処理を連続冷間圧延ラインでの１か月間の操業に適用した。また、裏面に噴射するガス量をより厳密に調整したところ、図３に例示したように、溶接部Ｍの形状は、鋼板Ｓのおもて面からの突出量ｅ１と裏面からの突出量ｅ２とが均等な形状、かつ鋼板Ｓのおもて面における圧延方向長さｆ１と裏面における圧延方向長さｆ２とが均等な形状となった（本発明２）。 As a welding process of the present invention, a certain amount of Ar gas is injected onto the front surface of the steel sheet S, and Ar gas variously adjusted to a smaller flow rate than the front surface is injected onto the back surface of the steel sheet S, so that the weld M The shape of the was controlled. Thereby, as for the shape of the welding part M, the protrusion amount e1 from the front surface of the steel plate S and the protrusion amount e2 from the back surface became a uniform shape (this invention 1). This treatment was applied to a one month operation on a continuous cold rolling line. Further, when the amount of gas injected to the back surface is adjusted more strictly, as illustrated in FIG. 3, the shape of the welded portion M is the amount of protrusion e1 from the front surface of the steel sheet S and the amount of protrusion e2 from the back surface. And the rolling direction length f1 on the front surface of the steel sheet S and the rolling direction length f2 on the back surface are uniform (Invention 2).
また、従来の溶接処理として、鋼板Ｓのおもて面／裏面ともに同じ流量でＡｒガスを噴射した。この場合、溶接部Ｍの形状は、図１に例示したように、鋼板Ｓのおもて面からの突出量ｅ１と裏面からの突出量ｅ２とが不均等な形状になった。 Further, as a conventional welding process, Ar gas was injected at the same flow rate on both the front surface and the back surface of the steel sheet S. In this case, as illustrated in FIG. 1, the shape of the weld M is such that the protruding amount e1 from the front surface of the steel sheet S and the protruding amount e2 from the back surface are uneven.
図６は、従来の溶接処理と本発明の溶接処理とによる溶接部Ｍの破断発生率を示す図である。図６に示すように、全溶接回数に対する溶接部Ｍの破断発生率が、従来の溶接処理では１．４２％であったのに対し、本発明１の溶接処理では０．６５％、本発明２の溶接処理では０．４０％であった。これにより、本発明の溶接処理では、溶接部Ｍの破断発生率が低下することが確認された。 FIG. 6 is a diagram showing the fracture occurrence rate of the weld M by the conventional welding process and the welding process of the present invention. As shown in FIG. 6, the fracture occurrence rate of the weld M with respect to the total number of weldings was 1.42% in the conventional welding process, while 0.65% in the welding process of the present invention 1, In the welding process No. 2, it was 0.40%. Thereby, in the welding process of this invention, it was confirmed that the fracture | rupture incidence rate of the welding part M falls.
以上、本発明者によってなされた発明を適用した実施の形態について説明したが、本実施形態による本発明の開示の一部をなす記述及び図面により本発明は限定されることはない。すなわち、本実施形態に基づいて当業者等によりなされる他の実施の形態、実施例および運用技術等は全て本発明の範疇に含まれる。 Although the embodiment to which the invention made by the present inventor is applied has been described above, the present invention is not limited by the description and the drawings that form a part of the disclosure of the present invention according to this embodiment. That is, other embodiments, examples, operational techniques, and the like made by those skilled in the art based on this embodiment are all included in the scope of the present invention.
１ 溶接装置
２ 発振器
３ 導光路
４ 集光部
５ ワイヤー供給装置
６ 制御部
Ｇ１ センターガス
Ｇ２ サイドガス
Ｇ３ バックガス
Ｌ レーザー光
Ｍ 溶接部
Ｓ 鋼鈑
DESCRIPTION OF SYMBOLS 1
Claims (2)
前記鋼板のおもて面に噴射する、レーザー溶接のアシストガスの種類および／または流量と、前記鋼板の裏面に噴射する、レーザー溶接のアシストガスの種類および／または流量とを、互いに異なるように調整して、前記端部間に形成される溶接部を、前記鋼板のおもて面からの突出量と裏面からの突出量とが均等な形状、かつ前記鋼板のおもて面における圧延方向長さと裏面における圧延方向長さとが均等な形状に突出させるよう制御する形状制御ステップを含み、前記溶接部を突出させた状態で前記鋼板が冷間圧延されることを特徴とする鋼板の溶接方法。 Prior to the cold rolling process, a method for welding steel sheets, in which end portions of two steel sheets to be subjected to the cold rolling process are welded to each other,
The type and / or flow rate of the assist gas for laser welding injected onto the front surface of the steel plate and the type and / or flow rate of the assist gas for laser welding injected onto the back surface of the steel plate are different from each other. The welded portion formed between the end portions is adjusted so that the protruding amount from the front surface of the steel plate and the protruding amount from the back surface are uniform, and the rolling direction on the front surface of the steel plate look including the shape control step of controlling so as to project in the rolling direction length and are equal shape in the length and the back surface, the welding of steel plates in which the steel sheet in a state of being projected the weld, characterized in that it is cold rolled Method.
前記鋼板のおもて面に噴射する、レーザー溶接のアシストガスの種類および／または流量と、前記鋼板の裏面に噴射する、レーザー溶接のアシストガスの種類および／または流量とを、互いに異なるように調整して、前記端部間に形成される溶接部を、前記鋼板のおもて面からの突出量と裏面からの突出量とが均等な形状、かつ前記鋼板のおもて面における圧延方向長さと裏面における圧延方向長さとが均等な形状に突出させるよう制御する形状制御手段を備え、前記溶接部を突出させた状態で前記鋼板が冷間圧延されるよう配置されていることを特徴とする鋼板の溶接装置。 Prior to the cold rolling process, a steel sheet welding apparatus that welds the ends of the two steel sheets to be subjected to the cold rolling process continuously,
The type and / or flow rate of the assist gas for laser welding injected onto the front surface of the steel plate and the type and / or flow rate of the assist gas for laser welding injected onto the back surface of the steel plate are different from each other. The welded portion formed between the end portions is adjusted so that the protruding amount from the front surface of the steel plate and the protruding amount from the back surface are uniform, and the rolling direction on the front surface of the steel plate with a shape control means and the rolling direction length in length and the rear surface is controlled so as to protrude into equal shape, the steel sheet in a state of being projected the weld and features that you have been arranged to be cold rolled Steel plate welding equipment.
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