JP4761993B2 - Manufacturing method of ferritic stainless steel welded pipe for spinning - Google Patents
Manufacturing method of ferritic stainless steel welded pipe for spinning Download PDFInfo
- Publication number
- JP4761993B2 JP4761993B2 JP2006036215A JP2006036215A JP4761993B2 JP 4761993 B2 JP4761993 B2 JP 4761993B2 JP 2006036215 A JP2006036215 A JP 2006036215A JP 2006036215 A JP2006036215 A JP 2006036215A JP 4761993 B2 JP4761993 B2 JP 4761993B2
- Authority
- JP
- Japan
- Prior art keywords
- less
- spinning
- stainless steel
- welded pipe
- tube
- 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.)
- Active
Links
- 238000009987 spinning Methods 0.000 title claims description 46
- 229910001220 stainless steel Inorganic materials 0.000 title claims description 24
- 238000004519 manufacturing process Methods 0.000 title claims description 13
- 238000003466 welding Methods 0.000 claims description 36
- 229910000831 Steel Inorganic materials 0.000 claims description 32
- 239000010959 steel Substances 0.000 claims description 32
- 239000011324 bead Substances 0.000 claims description 23
- 239000000463 material Substances 0.000 claims description 11
- 229910052757 nitrogen Inorganic materials 0.000 claims description 9
- 229910052799 carbon Inorganic materials 0.000 claims description 8
- 229910052761 rare earth metal Inorganic materials 0.000 claims description 6
- 229910052719 titanium Inorganic materials 0.000 claims description 6
- 229910052748 manganese Inorganic materials 0.000 claims description 5
- 229910052759 nickel Inorganic materials 0.000 claims description 5
- 229910052782 aluminium Inorganic materials 0.000 claims description 4
- 229910052758 niobium Inorganic materials 0.000 claims description 4
- 229910052710 silicon Inorganic materials 0.000 claims description 4
- 239000010935 stainless steel Substances 0.000 claims description 4
- 229910052802 copper Inorganic materials 0.000 claims description 3
- 229910052698 phosphorus Inorganic materials 0.000 claims description 3
- 239000012535 impurity Substances 0.000 claims description 2
- 229910000859 α-Fe Inorganic materials 0.000 claims 1
- 239000000203 mixture Substances 0.000 description 17
- 230000035515 penetration Effects 0.000 description 15
- 230000008602 contraction Effects 0.000 description 13
- 229910052751 metal Inorganic materials 0.000 description 7
- 239000002184 metal Substances 0.000 description 7
- 238000012545 processing Methods 0.000 description 6
- 238000011156 evaluation Methods 0.000 description 5
- 229910045601 alloy Inorganic materials 0.000 description 4
- 239000000956 alloy Substances 0.000 description 4
- 238000000034 method Methods 0.000 description 4
- 238000000137 annealing Methods 0.000 description 2
- 239000010953 base metal Substances 0.000 description 2
- 238000005336 cracking Methods 0.000 description 2
- 238000009863 impact test Methods 0.000 description 2
- 238000005554 pickling Methods 0.000 description 2
- 239000006104 solid solution Substances 0.000 description 2
- 238000009864 tensile test Methods 0.000 description 2
- 238000012360 testing method Methods 0.000 description 2
- 229910052721 tungsten Inorganic materials 0.000 description 2
- 230000015572 biosynthetic process Effects 0.000 description 1
- 239000003054 catalyst Substances 0.000 description 1
- 229910052804 chromium Inorganic materials 0.000 description 1
- 238000005097 cold rolling Methods 0.000 description 1
- 230000000052 comparative effect Effects 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 230000007423 decrease Effects 0.000 description 1
- 230000002950 deficient Effects 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- 238000005098 hot rolling Methods 0.000 description 1
- 238000011835 investigation Methods 0.000 description 1
- 238000003754 machining Methods 0.000 description 1
- 239000011159 matrix material Substances 0.000 description 1
- 239000000155 melt Substances 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 229910052750 molybdenum Inorganic materials 0.000 description 1
- 238000000465 moulding Methods 0.000 description 1
- 230000007704 transition Effects 0.000 description 1
Images
Landscapes
- Exhaust Silencers (AREA)
- Exhaust Gas After Treatment (AREA)
- Shaping Metal By Deep-Drawing, Or The Like (AREA)
Description
本発明は、優れたスピニング加工性を有するフェライト系ステンレス鋼溶接管の製造法であって、特に溶接条件に左右されにくく優れたスピニング性を安定して付与することのできるスピニング加工用フェライト系ステンレス鋼溶接管の製造法に関する。 The present invention is a method for producing a ferritic stainless steel welded pipe having excellent spinning workability , and is particularly ferritic stainless steel for spinning work that can be stably imparted with excellent spinning performance that is not easily affected by welding conditions. The present invention relates to a method for manufacturing a steel welded pipe.
排ガス経路部材のうち触媒ケースやサブマフラーの成形加工にスピニング加工を施す例が増えている。最近ではテーパー角度の大きい高縮径のスピニング加工に加え、偏心スピニングや傾斜スピニングなどの厳しい加工が施されることが多く、スピニング加工用の溶接管に要求される加工性はますます厳しくなる傾向にある。一方で、排ガス温度はますます高温化する傾向にあり、排ガス経路部材に要求される耐熱性のレベルも厳しくなっている。 An example in which spinning processing is applied to molding of a catalyst case and a sub-muffler among exhaust gas passage members is increasing. Recently, in addition to high-reduction spinning with a large taper angle, strict machining such as eccentric spinning and inclined spinning is often performed, and the workability required for welding pipes for spinning is becoming increasingly severe. It is in. On the other hand, the exhaust gas temperature tends to increase more and more, and the level of heat resistance required for the exhaust gas path member has become stricter.
溶接管のスピニング加工性を向上させるためには、鋼の成形性を確保することはもちろんのこと、溶接部の成形性や靱性を向上させることも重要となる。このような観点から、特許文献１には種々の合金元素の含有量を制限したフェライト系ステンレス鋼管が記載されている。また特許文献２には合金組成と溶接部の溶け込み深さを規定したフェライト系ステンレス鋼管が記載されている。 In order to improve the spinning workability of the welded pipe, it is important to improve the formability and toughness of the welded part as well as ensure the formability of the steel. From this point of view, Patent Document 1 describes a ferritic stainless steel pipe in which the content of various alloy elements is limited. Patent Document 2 describes a ferritic stainless steel pipe that defines the alloy composition and the penetration depth of the weld.
上記特許文献１の溶接管は、高温強度の確保に有効なＮｂが添加されておらず、排ガス温度の高温度化に必ずしも十分対応できるとは限らない。特許文献２の溶接管はＮｂまたはＴｉを含む鋼を用いてスピニング加工性の向上が図られているが、溶接部の溶け込み深さを大量生産現場において厳密にコントロールすることは必ずしも容易ではない。溶接ビードの形状は鋼の組成によって大きく変化しうるので、溶け込み深さを一定範囲に収めるには、鋼の組成変動に応じて煩雑な溶接条件の設定作業を必要とする場合がある。 In the welded pipe of Patent Document 1, Nb effective for ensuring high-temperature strength is not added, and the welded pipe cannot always cope with a high exhaust gas temperature. Although the welded pipe of Patent Document 2 is improved in spinning workability using steel containing Nb or Ti, it is not always easy to strictly control the penetration depth of the welded part at a mass production site. Since the shape of the weld bead can vary greatly depending on the composition of the steel, in order to keep the penetration depth within a certain range, it may be necessary to set complicated welding conditions in accordance with the variation in the composition of the steel.
また、これらの文献では縮管率（後述）が５０％のスピニング加工によりスピニング加工性を評価しているが、今後、排ガス流路部材においてはより高い縮管率でのスピニング加工の要求が高まると考えられ、５０％程度の縮管率をクリアできるというだけでは将来的なニーズに十分対応できない恐れがある。具体的には、縮管率５５％以上を安定して実現できるスピニング加工性を具備した溶接管が望まれる。 Further, in these documents, spinning workability is evaluated by spinning processing with a tube contraction rate (described later) of 50%, but in the future, there will be a demand for spinning processing with a higher tube contraction rate in the exhaust gas passage member. Therefore, there is a possibility that it will not be able to sufficiently meet future needs simply by being able to clear the tube contraction rate of about 50%. Specifically, a welded pipe having a spinning workability that can stably realize a contraction ratio of 55% or more is desired.
本発明はこのような現状に鑑み、縮管率５５％以上の優れたスピニング加工性を具備し、かつ高温強度および溶接部の靱性に優れたスピニング加工用ステンレス鋼溶接管を提供するために、鋼組成に依存した煩雑な溶接条件の設定を行う必要のない製造法を提供することを目的とする。 In view of such a current situation, the present invention provides a stainless steel welded pipe for spinning that has an excellent spinning workability of 55% or more in the shrinkage ratio and is excellent in high-temperature strength and toughness of the welded portion . It aims at providing the manufacturing method which does not need to set the complicated welding conditions depending on steel composition.
発明者らは種々検討の結果、素材鋼板の板厚（＝溶接管の肉厚）に応じて特定範囲に厳しく成分調整されたフェライト系ステンレス鋼を用いることによって、造管時の溶接条件を種々煩雑に変更することなく、スピニング加工性に優れた溶接管を安定して製造できることを見出した。 As a result of various studies, the inventors have used various ferritic stainless steels whose components are strictly adjusted to a specific range according to the thickness of the steel plate (= the thickness of the welded pipe), thereby varying the welding conditions during pipe making. The present inventors have found that a welded pipe excellent in spinning workability can be stably produced without complicated changes.
すなわち本発明では、質量％で、Ｃ：０.０３％以下、Ｓｉ：２.０％以下、Ｍｎ：２.０％以下、Ｐ：０.１％以下、Ｓ：０.０３％以下、Ｎｉ：１.０％以下、Ｃｒ：９〜２４％、Ｎｂ：０.０５〜０.６０％、Ｔｉ：０.０５〜０.３０％、Ａｌ：０.１５％以下、Ｎ：０.０３％以下、残部がＦｅおよび不可避的不純物からなり、下記（１）式および（２）式を満たし、かつ板厚ｔ（ただしｔは１.０〜２.２ｍｍ）に応じて下記（３）式を満たすように成分調整された素材鋼板を管状に成形して、溶接速度：３００ｍｍ／ｍｉｎ±３５％、かつ溶接電流：１３５Ａ±２０％の範囲で管の内面に裏ビードが現出するようにＴＩＧ溶接を行うことにより造管するスピニング加工用フェライト系ステンレス鋼溶接管の製造法が提供される。
Ｔｉ−４（Ｃ＋Ｎ）≧０ ……（１）
（Ｎｂ＋Ｔｉ）−８（Ｃ＋Ｎ）≧０ ……（２）
０.５≦ｙ／ｔ2≦２.０ ……（３）
ここで、ｔは素材鋼板の板厚（ｍｍ）、ｙは下記（４）式によるαを下記（５）式に代入して定まる値である。
α＝１５２２Ａｌ−２７３Ｔｉ−７０Ｍｎ＋２３Ｎｉ−２Ｓｉ＋４３、ただし左式によるαが負のときはα＝０とする ……（４）
ｙ＝（ｔ／２）0.5×（５.０２−０.０１４α−０.００１α2） ……（５）
That is, in the present invention, by mass, C: 0.03% or less, Si: 2.0% or less, Mn: 2.0% or less, P: 0.1% or less, S: 0.03% or less, Ni : 1.0% or less, Cr: 9 to 24%, Nb: 0.05 to 0.60%, Ti: 0.05 to 0.30%, Al: 0.15% or less, N: 0.03% Hereinafter, the balance consists of Fe and inevitable impurities , satisfies the following formulas (1) and (2), and the following formula (3) according to the thickness t (where t is 1.0 to 2.2 mm): TIG is formed so that a raw steel plate whose composition is adjusted to be filled is formed into a tubular shape, and a back bead appears on the inner surface of the tube at a welding speed of 300 mm / min ± 35% and a welding current of 135A ± 20%. Provided is a method for producing a ferritic stainless steel welded pipe for spinning, which is formed by welding .
Ti-4 (C + N) ≧ 0 (1)
(Nb + Ti) -8 (C + N) ≧ 0 (2)
0.5 ≦ y / t 2 ≦ 2.0 (3)
Here, t is a thickness (mm) of the material steel plate , and y is a value determined by substituting α in the following equation (5) by the following equation (4).
α = 1522Al-273Ti-70Mn + 23Ni-2Si + 43, provided that α = 0 when α according to the left equation is negative (4)
y = (t / 2) 0.5 × (5.02-0.014α-0.001α 2 ) (5)
前記素材鋼板としては、上記元素の他、さらに以下の元素を含有するものが採用できる。
・Ｖ：０.２％以下
・Ｍｏ：３.０％以下、Ｃｕ：３.０％以下、Ｗ：３.０％以下の１種以上
・ＲＥＭ（希土類元素）：０.１０％以下、Ｃａ：０.０１％以下の１種以上
・Ｂ：０.０１％以下
上記（１）式、（２）式、（４）式の元素記号の箇所には質量％で表された各元素の含有量の値が代入される。
As the material steel plate, those containing the following elements in addition to the above elements can be adopted.
V: 0.2% or less Mo: 3.0% or less, Cu: 3.0% or less, W: 3.0% or less REM (rare earth element): 0.10% or less, Ca : One or more of 0.01% or less B: 0.01% or less The content of each element expressed in mass% at the position of the element symbol in the above formulas (1), (2), and (4) The quantity value is substituted .
ここで、「管の内面に裏ビードが現出する」とは、トーチを管の外面側に配してＴＩＧ溶接する際、溶け込みが内面側に貫通し、内面に溶接金属の露出が認められることを意味する。 Here , “the back bead appears on the inner surface of the tube” means that when TIG welding is performed with the torch disposed on the outer surface side of the tube, the penetration penetrates to the inner surface side, and the exposed metal is exposed on the inner surface. Means that.
本発明によれば、組成を厳密に調整したフェライト系ステンレス鋼を用いたことによって、溶接造管時に組成に依存して溶接条件を適正化するといった煩雑な作業を行うことなく、裏ビードが現出するかどうかを確認する程度の条件決めを行うだけで、安定して優れたスピニング加工性を有する溶接管を製造することが可能になった。そのスピニング加工性は縮管率が５５％以上という高レベルのものである。また、本発明の溶接管は高温強度および溶接部の靱性にも優れる。したがって本発明は、スピニング加工性や耐熱性などに対する要求がますます厳しくなりつつある自動車排ガス流路部材に適したものである。 According to the present invention, the use of ferritic stainless steel whose composition is strictly adjusted allows the back bead to be formed without performing complicated operations such as optimizing welding conditions depending on the composition during welding pipe formation. It was possible to manufacture a welded pipe having stable and excellent spinning workability by simply determining the conditions for checking whether or not to release the steel. The spinning workability is at a high level with a tube contraction rate of 55% or more. In addition, the welded pipe of the present invention is excellent in high temperature strength and weld toughness. Therefore, the present invention is suitable for an automobile exhaust gas passage member whose requirements for spinning workability, heat resistance, and the like are becoming stricter.
発明者らは、スピニング加工性に及ぼすフェライト系ステンレス鋼の組成と造管時のＴＩＧ溶接条件との関係を詳細に調査してきた。その結果、スピニング加工性は、裏ビードが現出している場合において、溶接金属の溶け込み角度α（°）と板厚ｔ（ｍｍ）に依存することを見出した。そして、αとｔによって表される関数の値がある一定範囲となるときにスピニング加工性は顕著に向上することがわかった。 The inventors have investigated in detail the relationship between the composition of ferritic stainless steel and the TIG welding conditions during pipe making that affect spinning workability. As a result, it was found that the spinning workability depends on the penetration angle α (°) and the plate thickness t (mm) of the weld metal when the back bead appears. And it turned out that spinning workability improves notably when the value of the function represented by α and t falls within a certain range.
図１（ａ）に溶接管の外観を模式的に示す。溶接方向が管の長さ方向と平行になるようにＴＩＧによる突き合わせ溶接を行って溶接管を形成してある。図１（ａ）中に破線で示される溶接部断面を図１（ｂ）に拡大して模式的に示す。本発明の溶接管では図１（ｂ）に例示するように溶接金属が管内面まで到達しており、裏ビードが現出している。溶け込み角度αは図１（ｂ）に示すように、溶接方向に垂直な断面において、母材と溶接金属との界面（以下「母材溶接界面」という）の肉厚中心部での接線方向と、肉厚方向とのなす角度（°）として定義される。溶け込み角度αは通常、０°以上の値となる。 FIG. 1A schematically shows the appearance of the welded pipe. Butt welding by TIG is performed so that the welding direction is parallel to the length direction of the pipe, thereby forming a welded pipe. FIG. 1A schematically shows an enlarged cross section of a welded portion indicated by a broken line in FIG. In the welded pipe of the present invention, as shown in FIG. 1B, the weld metal reaches the inner surface of the pipe, and the back bead appears. As shown in FIG. 1 (b), the penetration angle α is the tangential direction at the thickness center of the interface between the base metal and the weld metal (hereinafter referred to as “base metal weld interface”) in a cross section perpendicular to the welding direction. , Defined as the angle (°) between the thickness direction. The penetration angle α is usually a value of 0 ° or more.
詳細な調査の結果、管の肉厚ｔ（ｍｍ）と溶け込み角度α（°）の関数ｙを（５）式のように設定したとき、ｔとｙの値が（３）式を満たす範囲で、当該フェライト系ステンレス鋼溶接管のスピニング加工性が顕著に改善されることが明らかになった。
ｙ＝（ｔ／２）0.5×（５.０２−０.０１４α−０.００１α2） ……（５）
０.５≦ｙ／ｔ2≦２.０ ……（３）
ただし、この関係は後述のような成分組成を有するフェライト系ステンレス鋼に適用され、溶接管の肉厚ｔが概ね１.０〜２.２ｍｍの範囲、かつスピニング加工前の素管の外径が概ね４０〜１６０ｍｍの範囲で精度良く評価できることが確認された。
As a result of detailed investigation, when the function y of the tube thickness t (mm) and the penetration angle α (°) is set as shown in the equation (5), the values of t and y satisfy the equation (3). It was revealed that the spinning workability of the ferritic stainless steel welded pipe was remarkably improved.
y = (t / 2) 0.5 × (5.02-0.014α-0.001α 2 ) (5)
0.5 ≦ y / t 2 ≦ 2.0 (3)
However, this relationship is applied to ferritic stainless steel having a component composition as described later, and the thickness t of the welded pipe is in the range of about 1.0 to 2.2 mm, and the outer diameter of the base pipe before spinning is set. It was confirmed that the evaluation can be performed with high accuracy in the range of approximately 40 to 160 mm.
スピニング加工性は縮管率によって評価できる。図２に、スピニング加工品のスピニング加工部近傍を管の長手方向に対して垂直方向から見た外観を模式的に示す。スピニング加工前の素管の外径（素管径）をΦ0、スピニング加工後の縮管部の外径（縮径）をΦ1とするとき、縮管率は下記（６）式によって定義される。
縮管率（％）＝（１−Φ1／Φ0）×１００ ……（６）
図２中に示すテーパー角を例えば５０°としたとき、縮管率５５％以上において管に割れが認められないフェライト系ステンレス鋼溶接管は、極めて良好なスピニング加工性を有していると評価できる。
Spinning workability can be evaluated by the tube contraction rate. FIG. 2 schematically shows the appearance of the vicinity of the spinning processed part of the spinning processed product viewed from the direction perpendicular to the longitudinal direction of the pipe. When the outer diameter of the raw pipe before spinning (raw pipe diameter) is Φ 0 and the outer diameter (reduced diameter) of the reduced pipe after spinning is Φ 1 , the reduced pipe ratio is defined by the following equation (6) Is done.
Reduced tube rate (%) = (1−Φ 1 / Φ 0 ) × 100 (6)
When the taper angle shown in FIG. 2 is, for example, 50 °, the ferritic stainless steel welded pipe in which cracks are not recognized at a pipe shrinkage ratio of 55% or more is evaluated as having very good spinning workability. it can.
さらに発明者らは詳細な研究により、前記の溶け込み角度α（°）は、フェライト系ステンレス鋼の成分組成と相関を有することを見出した。すなわち、各成分元素の含有量が後述の範囲にあり、かつ（１）式および（２）式を満たすフェライト系ステンレス鋼において、裏ビードが現出する溶接条件でＴＩＧ溶接を行った際の溶け込み角度αは（４）式によって精度良く推定できることがわかった。
α＝１５２２Ａｌ−２７３Ｔｉ−７０Ｍｎ＋２３Ｎｉ−２Ｓｉ＋４３、ただし左式によるαが負のときはα＝０とする ……（４）
上記数式にＡｌ、Ｔｉ、Ｍｎ、Ｎｉ、Ｓｉの各含有量を代入して算出されるαの値は負の値となることがあるが、その場合、溶接金属が管内面まで到達せず裏ビードが現出しないので、α＝０とする。
Furthermore, the inventors have found through a detailed study that the penetration angle α (°) has a correlation with the composition of the ferritic stainless steel. That is, in the ferritic stainless steel in which the content of each component element is in the range described below and satisfies the formulas (1) and (2), penetration when TIG welding is performed under the welding conditions in which the back bead appears. It was found that the angle α can be estimated with high accuracy by the equation (4).
α = 1522Al-273Ti-70Mn + 23Ni-2Si + 43, provided that α = 0 when α according to the left equation is negative (4)
The value of α calculated by substituting each content of Al, Ti, Mn, Ni, and Si into the above formula may be a negative value, but in this case, the weld metal does not reach the inner surface of the pipe and Since no bead appears, α = 0.
上記（４）式のとおり、ＴｉとＡｌが溶け込み角度αに大きな影響を及ぼす。すなわち、溶け込み角度αはＴｉが増大すると小さくなり、Ａｌが増大すると大きくなる。その原因は必ずしも明確ではないが、Ｔｉは溶融金属の粘性を上げ溶融部の表面張力を増大させることにより溶け込みが深くなるように作用し、逆にＡｌは溶融金属の粘性を下げ溶融部の表面張力を低下させることにより溶け込みが浅くなるように作用することが要因として考えられる。またＭｎ、Ｎｉ、Ｓｉも溶け込み性に影響を及ぼす。 As shown in the above equation (4), Ti and Al have a great influence on the penetration angle α. That is, the penetration angle α decreases as Ti increases, and increases as Al increases. The cause is not necessarily clear, but Ti acts to increase the melt tension by increasing the viscosity of the molten metal and increasing the surface tension of the melted area. It is considered that the factor is that the penetration becomes shallow by lowering the tension. Mn, Ni, and Si also affect the solubility.
図３には、後述表１のＮｏ.Ａ２に示される１４Ｃｒ−１Ｓｉ−０.４Ｎｂ鋼をベースとした板厚１.０〜２.２ｍｍの範囲の多くの素材鋼板を用いて、後述のようにＴＩＧ溶接で素管径１３０ｍｍの溶接管を製造し、これをテーパー角５０°のスピニング加工試験に供したときの、前記（３）式によるｙ／ｔ2値と最大縮管率の関係を示してある。最大縮管率は、管に割れが生じはじめるときの前記（６）式による縮管率である。図３からわかるように、（３）式によるｙ／ｔ2値が０.５〜２.０の範囲において最大縮管率は顕著に向上し、縮管率５５％以上のスピニング加工性が安定して得られる。後述の組成範囲にある種々の成分系の鋼についても、同様の結果が得られている。 In FIG. 3, as described later, a large number of steel plates having a thickness of 1.0 to 2.2 mm based on 14Cr-1Si-0.4Nb steel shown in No. A2 of Table 1 described later are used. The relationship between the y / t 2 value according to the above equation (3) and the maximum tube contraction rate when a welded tube with a tube diameter of 130 mm is manufactured by TIG welding and subjected to a spinning processing test with a taper angle of 50 °. It is shown. The maximum tube contraction rate is the tube contraction rate according to the formula (6) when cracks start to occur in the tube. As can be seen from FIG. 3, the maximum tube contraction rate is remarkably improved in the range of y / t 2 value of 0.5 to 2.0 according to the equation (3), and the spinning workability with the tube contraction rate of 55% or more is stable. Is obtained. Similar results are obtained for various component steels in the composition range described below.
このような優れたスピニング加工性を安定して呈するフェライト系ステンレス鋼溶接管を製造する方法としては、まず、目的とする溶接管の肉厚ｔに応じて（３）式を満たす組成にコントロールされた素材鋼板を用意することが重要である。ただし、各合金元素の含有量は後述の成分組成範囲とする必要がある。なお本発明では、素材鋼板の板厚と、それを造管して得られる溶接管の肉厚は、等しいとみなして構わない。 As a method for producing a ferritic stainless steel welded tube that stably exhibits such excellent spinning workability, first, the composition satisfying the formula (3) is controlled according to the thickness t of the intended welded tube. It is important to prepare a raw steel plate. However, the content of each alloy element needs to be within the component composition range described below. In the present invention, the plate thickness of the material steel plate and the thickness of the welded pipe obtained by pipe-forming it may be regarded as equal.
次に、素材鋼板を例えば連続ラインでロール成形等により管状に成形していき、ＴＩＧによる突き合わせ溶接を行う方法で造管する。その際、溶接管の肉厚ｔが概ね１.０〜２.２ｍｍの範囲では、以下の溶接条件を採用すればよい。
・溶接速度：３００ｍｍ／ｍｉｎ±３５％
・溶接電流：１３５Ａ±２０％
造管作業中には、裏ビードが現出しているかどうかを確認し、例えば溶接速度３００ｍｍ／ｍｉｎ、溶接電流１３５Ａの基本条件において裏ビードが現出しなければ、上記許容範囲内で条件を変動させて裏ビードが現出するように条件を調整すればよい。このような簡単な操作だけで、優れたスピニング加工性を具備する溶接管を製造することができる。歩留りも、最初の条件出しに使用したわずかな部分だけを除去すれば済むため、大きく低下することはない。
Next, the raw steel plate is formed into a tubular shape by roll forming or the like in a continuous line, for example, and is formed by a method of performing butt welding by TIG. At this time, the following welding conditions may be employed in the range where the thickness t of the welded tube is approximately 1.0 to 2.2 mm.
・ Welding speed: 300mm / min ± 35%
・ Welding current: 135A ± 20%
During pipe making work, check whether the back bead has appeared. For example, if the back bead does not appear under the basic conditions of a welding speed of 300 mm / min and a welding current of 135 A, the conditions are varied within the above allowable range. Adjust the conditions so that the back bead appears. Only with such a simple operation, a welded pipe having excellent spinning workability can be manufactured. Yield is not greatly reduced because only a small portion used for initial condition determination needs to be removed.
〔成分組成〕
本発明では、自動車の排ガス流路部材用途を考慮して、高温強度を確保したＮｂ添加フェライト系ステンレス鋼を採用する。Ｎｂはマトリクス中に固溶状態で存在することによってステンレス鋼の高温強度を向上させる他、本発明では溶接部および母材の靱性を損なわないようにＣ、Ｎを固定する作用も担う。ただしＣ、Ｎの固定によって固溶Ｎｂが過剰に消費されると高温強度の向上が図れないので、本発明ではＣ、Ｎの固定にはＴｉを積極的に利用する。すなわち、Ｔｉを０.０５質量％以上、かつ下記（１）式を満たすように含有させてＣ、Ｎの大部分を固着させた上で、０.０５質量％以上のＮｂを添加する。０.１５質量％以上のＮｂ含有量を確保することが一層好ましい。
Ｔｉ−４（Ｃ＋Ｎ）≧０ ……（１）
(Component composition)
In the present invention, Nb-added ferritic stainless steel that secures high-temperature strength is employed in consideration of the use of an exhaust gas passage member for automobiles. In addition to improving the high temperature strength of stainless steel by Nb being present in a solid solution state in the matrix, Nb is also responsible for fixing C and N so as not to impair the toughness of the weld and base material. However, when solid solution Nb is excessively consumed by fixing C and N, the high temperature strength cannot be improved. Therefore, in the present invention, Ti is positively used for fixing C and N. That is, Ti is added in an amount of 0.05% by mass or more and satisfies the following formula (1) to fix most of C and N, and then 0.05% by mass or more of Nb is added. It is more preferable to secure an Nb content of 0.15% by mass or more.
Ti-4 (C + N) ≧ 0 (1)
溶接部と母材との機械的性質に大幅な差が生じないように、ＣおよびＮの含有量はできるだけ低く抑える必要がある。具体的にはＣ、Ｎともそれぞれ０.０３質量％以下の含有量範囲とし、かつ下記（２）式を満たすＴｉ、Ｎｂを含有させることによりＣ、Ｎを固定する。
（Ｎｂ＋Ｔｉ）−８（Ｃ＋Ｎ）≧０ ……（２）
It is necessary to keep the contents of C and N as low as possible so that there is no significant difference between the mechanical properties of the weld and the base material. Specifically, C and N are both fixed to 0.03 mass% or less, and Ti and Nb satisfying the following formula (2) are contained to fix C and N.
(Nb + Ti) -8 (C + N) ≧ 0 (2)
Ａｌは脱酸剤として添加されるが、前述の（４）式からわかるように溶接部の溶け込み角度αを増大させる作用が大きい元素であるため、過剰にＡｌを添加するとスピニング加工性に優れた溶接管を得ることが難しくなる。したがってＡｌ含有量は０.１５質量％以下に制限される。 Al is added as a deoxidizer, but as can be seen from the above-described equation (4), it is an element that has a large effect of increasing the penetration angle α of the welded portion. It becomes difficult to obtain a welded tube. Therefore, the Al content is limited to 0.15% by mass or less.
Ｃｒは耐食性の確保に必須の元素であり、少なくとも９質量％以上の含有量とする。ただし、過剰のＣｒ含有は加工性等を阻害する要因になるので、Ｃｒ含有量は２４質量％以下とする。 Cr is an essential element for ensuring corrosion resistance and has a content of at least 9% by mass. However, since excessive Cr content becomes a factor which hinders workability etc., Cr content shall be 24 mass% or less.
その他の合金元素は、母材および溶接部の靱性を損なわない範囲で含有させることができる。具体的には、Ｓｉ：２.０％以下、Ｍｎ：２.０％以下、Ｐ：０.１％以下、Ｓ：０.０３％以下、Ｎｉ：１.０％以下の範囲でこれらの含有が許容される。これらの他にも各種特性を向上させるために、必要に応じてＶ：０.２％以下、あるいはＭｏ：３.０％以下、Ｃｕ：３.０％以下、Ｗ：３.０％以下、Ｖ：０.２％以下の１種以上、あるいはＲＥＭ（希土類元素）：０.１０％以下、Ｃａ：０.０１％以下の１種以上、あるいはＢ：０.０１％以下の範囲でこれらの元素を含有することができる。 Other alloy elements can be contained within a range that does not impair the toughness of the base material and the weld. Specifically, Si is not more than 2.0%, Mn is not more than 2.0%, P is not more than 0.1%, S is not more than 0.03%, and Ni is not more than 1.0%. Is acceptable. In addition to these, in order to improve various characteristics, V: 0.2% or less, Mo: 3.0% or less, Cu: 3.0% or less, W: 3.0% or less, if necessary, V: one or more of 0.2% or less, or REM (rare earth element): 0.10% or less, Ca: one or more of 0.01% or less, or B: 0.01% or less It can contain elements.
本発明の溶接管は、以上の成分組成を有するフェライト系ステンレス鋼を溶製し、通常の工程により板厚１.０〜２.２ｍｍの焼鈍鋼板を製造し、これを一般的な溶接造管ラインでＴＩＧ溶接により造管することによって製造することができる。 The welded pipe of the present invention is manufactured by melting ferritic stainless steel having the above composition and producing an annealed steel sheet having a thickness of 1.0 to 2.2 mm by a normal process. It can be manufactured by making a pipe by TIG welding in a line.
表１に示す鋼を溶製し、熱間圧延、焼鈍、酸洗、冷間圧延、焼鈍、酸洗を経て、板厚１.２〜２．０ｍｍの素材鋼板を得た。各素材鋼板をロール成形により管状にしていきＴＩＧにより突き合わせ溶接を行う設備を備えた連続造管ラインに通して、外径１３０ｍｍの溶接管を製造した。溶接条件は、溶接速度３００ｍｍ／ｍｉｎ±３５％、溶接電流１３５Ａ±２０％の範囲で、裏ビードが現出する条件とした。 The steel shown in Table 1 was melted and subjected to hot rolling, annealing, pickling, cold rolling, annealing, and pickling to obtain a raw steel plate having a thickness of 1.2 to 2.0 mm. Each material steel plate was formed into a tubular shape by roll forming, and passed through a continuous tube forming line equipped with equipment for performing butt welding by TIG, to manufacture a welded tube having an outer diameter of 130 mm. The welding conditions were such that the back bead appeared in the range of a welding speed of 300 mm / min ± 35% and a welding current of 135A ± 20%.
〔縮管性評価〕
各溶接管を素管として縮管率５５％、テーパー角５０°で外径５８.５ｍｍまで１２パスにてスピニング加工を試みた。縮管率５５％まで割れを生じずにスピニング加工ができたものを○（良好）、加工途中で割れが生じたものを×（不良）として縮管性を評価した。
[Evaluation of ductility]
Spinning processing was attempted in 12 passes from each welded tube to a base tube with a reduction rate of 55%, a taper angle of 50 °, and an outer diameter of 58.5 mm. The tube shrinkage was evaluated as ○ (good) when the spinning process was completed without cracking up to a tube contraction rate of 55%, and x (bad) when cracking occurred during the processing.
〔ビード靱性評価〕
上記の各素材鋼板（造管工程に供する前の鋼板）から採取したサンプルを用いて、それぞれ造管時と同じ溶接速度および溶接電流の条件でＴＩＧによるなめづけ溶接（板の上にそのままビードを走らせる溶接実験）を行い、得られた溶接後の鋼板から溶接ビード部を中央に含むＶノッチシャルピー衝撃試験片を作製した。ＪＩＳ Ｚ２２４２に準拠したシャルピー衝撃試験を行い、延性・脆性の遷移温度が０℃以下のものを○（良好）、０℃より高いものを×（不良）と評価した。
[Evaluation of bead toughness]
Using samples taken from each of the above-mentioned raw steel plates (steel plates before being used in the pipe making process), tanning welding with TIG at the same welding speed and welding current conditions as in pipe making (with beads directly on the plate) A V-notch Charpy impact test piece including a weld bead portion at the center was produced from the obtained welded steel plate. A Charpy impact test in accordance with JIS Z2242 was conducted, and those having a ductile / brittle transition temperature of 0 ° C. or lower were evaluated as ◯ (good), and those higher than 0 ° C. were evaluated as × (bad).
〔高温強度評価〕
上記のなめづけ溶接を行った鋼板からビード部を引張方向に対して垂直方向に有する引張試験片を作製し、当該試験片を大気中で８００℃に加熱した状態でＪＩＳ Ｇ０５６７に準拠した引張試験を行い、ビード部の０.２％耐力を測定した。８００℃の０.２％耐力が２０ＭＰａ以上のものを○（良好）、２０ＭＰａ未満のものを×（不良）と評価した。
表２に、各鋼について（４）式により算出される溶け込み角度α、板厚ｔ、（５）式により算出されるｙ値、（３）式により算出されるｙ／ｔ2値、および上記評価結果を示す。
[High temperature strength evaluation]
A tensile test piece having a bead portion in a direction perpendicular to the tensile direction is produced from the steel plate subjected to the tanning welding, and the tensile test in accordance with JIS G0567 is performed in a state where the test piece is heated to 800 ° C. in the atmosphere. And 0.2% proof stress of the bead portion was measured. Those having a 0.2% proof stress at 800 ° C. of 20 MPa or more were evaluated as ◯ (good), and those with less than 20 MPa were evaluated as × (defective).
Table 2 shows the penetration angle α calculated by the equation (4), the thickness t, the y value calculated by the equation (5), the y / t 2 value calculated by the equation (3), and the above. An evaluation result is shown.
表２からわかるように、本発明例の溶接管はいずれもｙ／ｔ2値が０.５〜２.０の範囲に収まるように成分調整されており、縮管性、ビード靱性および高温強度に優れたものであった。 As can be seen from Table 2, the components of the welded pipes of the present invention were adjusted so that the y / t 2 value was within the range of 0.5 to 2.0, and the tube shrinkability, bead toughness, and high temperature strength were high. It was excellent.
これに対し、比較例であるＮｏ.Ｂ１はＡｌ含有量が多すぎたことによりα値が過大になり、ｙ／ｔ2値が適正範囲を外れて縮管性に劣った。Ｎｏ.Ｂ２はＴｉ含有量が少なすぎたことによりα値が大きくなり、ｙ／ｔ2値が適正範囲を外れて縮管性およびビード靱性に劣った。Ｎｏ.Ｂ３はｙ／ｔ2値は適正であるが、Ｎｂ含有量が多すぎたことにより縮管性およびビード靱性に劣った。Ｎｏ.Ｂ４は逆にＮｂ含有量が少なすぎたことにより高温強度が低かった。Ｎｏ.Ｂ５は（１）式を満たさない組成を有し、ビード靱性に劣った。Ｎｏ.Ｂ６は（２）式を満たさない組成を有し、縮管性と高温強度に劣った。Ｎｏ.Ｂ７はＳｉ含有量が多すぎたためビード靱性に劣った。 On the other hand, No. B1, which is a comparative example, had an excessively high α value due to too much Al content, and the y / t 2 value was out of the proper range and was inferior in tube shrinkability. No. B2 had a large α value due to too little Ti content, and the y / t 2 value was out of the proper range and was inferior in tube shrinkage and bead toughness. No. B3 had an appropriate y / t 2 value, but was inferior in tube shrinkage and bead toughness due to excessive Nb content. On the other hand, No. B4 had a low high-temperature strength due to too little Nb content. No. B5 had a composition not satisfying the formula (1) and was inferior in bead toughness. No. B6 had a composition that did not satisfy the formula (2), and was inferior in tube shrinkability and high-temperature strength. No. B7 was inferior in bead toughness because of excessive Si content.
Claims (5)
Ｔｉ−４（Ｃ＋Ｎ）≧０ ……（１）
（Ｎｂ＋Ｔｉ）−８（Ｃ＋Ｎ）≧０ ……（２）
０.５≦ｙ／ｔ2≦２.０ ……（３）
ここで、ｔは素材鋼板の板厚（ｍｍ）、ｙは下記（４）式によるαを下記（５）式に代入して定まる値である。
α＝１５２２Ａｌ−２７３Ｔｉ−７０Ｍｎ＋２３Ｎｉ−２Ｓｉ＋４３、ただし左式によるαが負のときはα＝０とする ……（４）
ｙ＝（ｔ／２）0.5×（５.０２−０.０１４α−０.００１α2） ……（５） In mass%, C: 0.03% or less, Si: 2.0% or less, Mn: 2.0% or less, P: 0.1% or less, S: 0.03% or less, Ni: 1.0% Hereinafter, Cr: 9 to 24%, Nb: 0.05 to 0.60%, Ti: 0.05 to 0.30%, Al: 0.15% or less, N: 0.03% or less, the balance being Fe And inevitable impurities, satisfying the following formulas (1) and (2), and adjusting the components so as to satisfy the following formula (3) according to the thickness t (where t is 1.0 to 2.2 mm) By forming the formed steel plate into a tube and performing TIG welding so that the back bead appears on the inner surface of the tube at a welding speed of 300 mm / min ± 35% and a welding current of 135 A ± 20%. Manufacturing method for ferritic stainless steel welded pipes for spinning.
Ti-4 (C + N) ≧ 0 (1)
(Nb + Ti) -8 (C + N) ≧ 0 (2)
0.5 ≦ y / t 2 ≦ 2.0 (3)
Here, t is a thickness (mm) of the material steel plate, and y is a value determined by substituting α in the following equation (5) by the following equation (4).
α = 1522Al-273Ti-70Mn + 23Ni-2Si + 43, provided that α = 0 when α according to the left equation is negative (4)
y = (t / 2) 0.5 × (5.02-0.014α-0.001α 2 ) (5)
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2006036215A JP4761993B2 (en) | 2006-02-14 | 2006-02-14 | Manufacturing method of ferritic stainless steel welded pipe for spinning |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2006036215A JP4761993B2 (en) | 2006-02-14 | 2006-02-14 | Manufacturing method of ferritic stainless steel welded pipe for spinning |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JP2007217716A JP2007217716A (en) | 2007-08-30 |
| JP4761993B2 true JP4761993B2 (en) | 2011-08-31 |
Family
ID=38495315
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP2006036215A Active JP4761993B2 (en) | 2006-02-14 | 2006-02-14 | Manufacturing method of ferritic stainless steel welded pipe for spinning |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP4761993B2 (en) |
Families Citing this family (17)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US7922065B2 (en) | 2004-08-02 | 2011-04-12 | Ati Properties, Inc. | Corrosion resistant fluid conducting parts, methods of making corrosion resistant fluid conducting parts and equipment and parts replacement methods utilizing corrosion resistant fluid conducting parts |
| JP5151223B2 (en) * | 2007-04-13 | 2013-02-27 | Ｊｆｅスチール株式会社 | Ferritic stainless steel sheet excellent in spinning workability and manufacturing method thereof |
| JP5563203B2 (en) * | 2008-03-12 | 2014-07-30 | 新日鐵住金ステンレス株式会社 | Ferritic stainless steel with excellent corrosion resistance in urea water and ferritic stainless steel for urea SCR system |
| JP5625765B2 (en) * | 2010-11-05 | 2014-11-19 | Ｊｆｅスチール株式会社 | Chrome-containing ferritic steel sheet for solar cell substrates |
| US20140065005A1 (en) * | 2012-08-31 | 2014-03-06 | Eizo Yoshitake | Ferritic Stainless Steel with Excellent Oxidation Resistance, Good High Temperature Strength, and Good Formability |
| CN103775184A (en) * | 2012-10-26 | 2014-05-07 | 重庆长安汽车股份有限公司 | Longitudinally arranged engine exhaust branch pipe assembly |
| FI124995B (en) * | 2012-11-20 | 2015-04-15 | Outokumpu Oy | Ferritic stainless steel |
| US10118259B1 (en) | 2012-12-11 | 2018-11-06 | Ati Properties Llc | Corrosion resistant bimetallic tube manufactured by a two-step process |
| US20160168673A1 (en) * | 2013-07-29 | 2016-06-16 | Jfe Steel Corporation | Ferritic stainless steel having excellent corrosion resistance of weld zone |
| MX2017000077A (en) * | 2014-06-27 | 2017-05-30 | Ati Properties Llc | Flowforming corrosion resistant alloy tubes and tube manufactured thereby. |
| JP6146401B2 (en) * | 2014-08-14 | 2017-06-14 | Ｊｆｅスチール株式会社 | Ferritic stainless steel sheet |
| JP6146400B2 (en) * | 2014-08-14 | 2017-06-14 | Ｊｆｅスチール株式会社 | Ferritic stainless steel sheet |
| EP3187609B1 (en) * | 2014-08-29 | 2021-10-06 | JFE Steel Corporation | Ferritic stainless steel foil and production method for same |
| JP6390594B2 (en) * | 2015-11-13 | 2018-09-19 | Ｊｆｅスチール株式会社 | Ferritic stainless steel |
| JP6604895B2 (en) * | 2016-04-13 | 2019-11-13 | 日立造船株式会社 | Manufacturing method of exhaust gas treatment device |
| CN107470864B (en) * | 2017-08-03 | 2019-05-14 | 浙江汇金机械制造有限公司 | A kind of steel cylinder flow forming and molding process |
| CN111519087B (en) * | 2020-05-27 | 2021-10-22 | 湖南大学 | Preparation method of TiC particle reinforced high-chromium cast iron alloy material |
Family Cites Families (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP4400058B2 (en) * | 2003-02-13 | 2010-01-20 | Ｊｆｅスチール株式会社 | Ferritic stainless steel welded pipe with excellent spinning processability |
| JP4309293B2 (en) * | 2004-01-19 | 2009-08-05 | 新日鐵住金ステンレス株式会社 | Ferritic stainless steel for automotive exhaust system parts |
| JP4241431B2 (en) * | 2004-02-26 | 2009-03-18 | Ｊｆｅスチール株式会社 | Ferritic stainless steel |
-
2006
- 2006-02-14 JP JP2006036215A patent/JP4761993B2/en active Active
Also Published As
| Publication number | Publication date |
|---|---|
| JP2007217716A (en) | 2007-08-30 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| JP4761993B2 (en) | Manufacturing method of ferritic stainless steel welded pipe for spinning | |
| JP4258678B1 (en) | Austenitic stainless steel | |
| JP5050863B2 (en) | Ferritic stainless steel sheet for water heaters | |
| JP4258679B1 (en) | Austenitic stainless steel | |
| JP6197885B2 (en) | Welding material for Ni-base heat-resistant alloy, weld metal and welded joint using the same | |
| KR101674341B1 (en) | Electric-resistance-welded steel pipe with excellent weld quality and method for producing same | |
| JP5641741B2 (en) | High strength Zn-Al-Mg plated steel sheet with excellent bendability and molten metal embrittlement resistance | |
| KR101899229B1 (en) | Ferritic stainless steel | |
| JP5176591B2 (en) | Welded steel pipe with excellent weld heat-affected zone toughness | |
| JP5630322B2 (en) | High-tensile steel plate with excellent toughness and manufacturing method thereof | |
| JP2018053281A (en) | Rectangular steel tube | |
| JP6256655B2 (en) | Steel sheet for structural pipe, method for manufacturing steel sheet for structural pipe, and structural pipe | |
| JP5509654B2 (en) | High-strength steel sheet excellent in PWHT resistance and uniform elongation characteristics and method for producing the same | |
| US10400318B2 (en) | Ferritic stainless steel | |
| KR20230042371A (en) | Welded joints and manufacturing methods of welded joints | |
| JP3322097B2 (en) | High strength, high corrosion resistant ferritic steel welding material with excellent weldability | |
| WO2019070002A1 (en) | Welding material for austenitic heat-resistant steel, weld metal and weld structure, and method for manufacturing weld metal and weld structure | |
| JP5741454B2 (en) | Ni-added steel sheet excellent in toughness and productivity in which Charpy test value at −196 ° C. is 100 J or more for both base metal and welded joint, and manufacturing method thereof | |
| JP2010235989A (en) | High strength zn-al-mg based plated steel sheet excellent in liquid metal embrittlement resistant characteristics and production method therefor | |
| JP4193308B2 (en) | Low carbon ferrite-martensitic duplex stainless steel welded steel pipe with excellent resistance to sulfide stress cracking | |
| JP6354281B2 (en) | Ferritic heat resistant steel pipe | |
| WO2020170928A1 (en) | Welding material for high-cr ferritic heat-resistant steels | |
| JP5489504B2 (en) | Stainless steel welded structure with excellent weld toughness and stainless steel plate for welding | |
| JP2008188641A (en) | High-strength welded steel tube of excellent welding softening resistance and excellent fatigue characteristic | |
| JP5223295B2 (en) | Refractory H-shaped steel with excellent reheat embrittlement resistance and method for producing the same |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| A621 | Written request for application examination |
Free format text: JAPANESE INTERMEDIATE CODE: A621 Effective date: 20090119 |
|
| A977 | Report on retrieval |
Free format text: JAPANESE INTERMEDIATE CODE: A971007 Effective date: 20110210 |
|
| A131 | Notification of reasons for refusal |
Free format text: JAPANESE INTERMEDIATE CODE: A131 Effective date: 20110215 |
|
| A521 | Request for written amendment filed |
Free format text: JAPANESE INTERMEDIATE CODE: A523 Effective date: 20110418 |
|
| TRDD | Decision of grant or rejection written | ||
| A01 | Written decision to grant a patent or to grant a registration (utility model) |
Free format text: JAPANESE INTERMEDIATE CODE: A01 Effective date: 20110607 |
|
| A01 | Written decision to grant a patent or to grant a registration (utility model) |
Free format text: JAPANESE INTERMEDIATE CODE: A01 |
|
| A61 | First payment of annual fees (during grant procedure) |
Free format text: JAPANESE INTERMEDIATE CODE: A61 Effective date: 20110607 |
|
| FPAY | Renewal fee payment (event date is renewal date of database) |
Free format text: PAYMENT UNTIL: 20140617 Year of fee payment: 3 |
|
| R150 | Certificate of patent or registration of utility model |
Ref document number: 4761993 Country of ref document: JP Free format text: JAPANESE INTERMEDIATE CODE: R150 Free format text: JAPANESE INTERMEDIATE CODE: R150 |
|
| R250 | Receipt of annual fees |
Free format text: JAPANESE INTERMEDIATE CODE: R250 |
|
| S111 | Request for change of ownership or part of ownership |
Free format text: JAPANESE INTERMEDIATE CODE: R313111 |
|
| S533 | Written request for registration of change of name |
Free format text: JAPANESE INTERMEDIATE CODE: R313533 |
|
| R350 | Written notification of registration of transfer |
Free format text: JAPANESE INTERMEDIATE CODE: R350 |
|
| R360 | Written notification for declining of transfer of rights |
Free format text: JAPANESE INTERMEDIATE CODE: R360 |
|
| R360 | Written notification for declining of transfer of rights |
Free format text: JAPANESE INTERMEDIATE CODE: R360 |
|
| R371 | Transfer withdrawn |
Free format text: JAPANESE INTERMEDIATE CODE: R371 |
|
| S111 | Request for change of ownership or part of ownership |
Free format text: JAPANESE INTERMEDIATE CODE: R313111 |
|
| R350 | Written notification of registration of transfer |
Free format text: JAPANESE INTERMEDIATE CODE: R350 |
|
| R250 | Receipt of annual fees |
Free format text: JAPANESE INTERMEDIATE CODE: R250 |
|
| R250 | Receipt of annual fees |
Free format text: JAPANESE INTERMEDIATE CODE: R250 |
|
| R250 | Receipt of annual fees |
Free format text: JAPANESE INTERMEDIATE CODE: R250 |
|
| R250 | Receipt of annual fees |
Free format text: JAPANESE INTERMEDIATE CODE: R250 |
|
| R250 | Receipt of annual fees |
Free format text: JAPANESE INTERMEDIATE CODE: R250 |