JP3533837B2 - Refractory electric resistance welded steel pipe for construction with excellent plating resistance - Google Patents
Refractory electric resistance welded steel pipe for construction with excellent plating resistanceInfo
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- JP3533837B2 JP3533837B2 JP21240896A JP21240896A JP3533837B2 JP 3533837 B2 JP3533837 B2 JP 3533837B2 JP 21240896 A JP21240896 A JP 21240896A JP 21240896 A JP21240896 A JP 21240896A JP 3533837 B2 JP3533837 B2 JP 3533837B2
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Description
【発明の詳細な説明】
【０００１】
【発明の属する技術分野】本発明は高温での耐力低下が
少なく、かつ良好な溶融Ｚｎめっき外観を有する耐めっ
き焼け性に優れた丸管・角管などの建築用耐火電縫溶接
鋼管に関する。
【０００２】
【従来の技術】昭和62年に建築物の耐火設計法が見直さ
れ、火災時の鋼材に対する許容温度の項目が外された。
これに伴い、高温下での耐力低下が少ない建材が開発さ
れ、この建材は火災時の到達温度が低い場所においては
耐火被覆を低減し、あるいは無耐火被覆で使用されてい
る。特開平2-197520号公報は、極低炭素鋼にＴｉまたは
／かつＮｂを添加し、かつ多量のＣｕを添加した成分系
の鋼をＣｕによる高温割れが生じないように、かつ所定
の特性を十分付与させるような特定の熱延条件で熱延を
行い、さらに場合によってはＰで強度を調整し、また、
高温割れに対してはＮｉ添加で補強して、耐火性に優れ
た建築用低降伏比亜鉛めっき鋼板の製造方法が開示され
ている。
【０００３】現在の亜鉛めっき処理では440-460 ℃の亜
鉛浴に約5 分間浸漬するのが一般的方法で、これにより
鋼の表面に、光沢面をもつ連続的でち密かつ均一で、加
工作業に適した厚みをもつめっき層が形成される。
【０００４】しかし、近年ケイ素を含む新鋼種が市場に
出現してから事態が変わってきた。これら新鋼種の発展
に伴い必然的に、製鋼所では在来の旧鋳造法に代ってキ
リング、連続鋳造法を中心とする新しい鋳造法が発達
し、また金属構造部門では、機械的特性の優れた鋼種の
用途が益々拡がり、中でも含ケイ素鋼は最も作業が容易
なためその中心となっている。
【０００５】亜鉛めっき部門に限って言えば、ケイ素の
存在は、現在のところ現場で幾つかの難問題を生じてい
る。これまでの経験では、含ケイ素鋼の亜鉛めっきで
は、表面欠陥をもち、灰色で、密着性の劣る、厚みの過
大なめっき層が形成されることが判っている。
【０００６】Ｊ．ＰＥＬＥＲＩＮ，Ｊ．ＨＯＦＦＭＡ
Ｎ，Ｄｒ．Ｖ．ＬＥＲＯＹらの「軟鋼の溶融亜鉛めっき
におけるケイ素及びリンの影響」についての研究（”鉛
と亜鉛”第107 号 1982年5 月に掲載）によれば、上記
の一般的な方法で鋼板に亜鉛めっきを施す場合、 0.1％
＜Ｓｉ％＋ 2.5Ｐ％＜ 0.2％、さらに 0.3％＜Ｓｉ％＋
2.5 Ｐ％の範囲でドブ漬けめっき時のＦｅ−Ｚｎ合金化
が異常に促進され”めっき焼け”とよばれる外観不良
（光沢不良）が起こること、さらに、Ｓｉ（及びＰ）含
有量が最適範囲（Ｓｉ％＜0.04％，Ｓｉ％＋2.5 Ｐ％＜
0.09 ％）では、Ｆｅ−Ｚｎ合金層が鋼管上に比較的ゆ
っくりと均一に生成し、めっき最表層は合金化しておら
ず、金属光沢が得られることが示されている。
【０００７】
【発明が解決しようとする課題】しかし、上記の特開平
2-197520号公報の技術は、機械的特性に優れた含ケイ素
鋼を対象としたものではない。また、Ｊ．ＰＥＬＥＲＩ
Ｎ，Ｊ．ＨＯＦＦＭＡＮ，Ｄｒ．Ｖ．ＬＥＲＯＹらの研
究は、鋼板の高温強度を高めることを目的とした含ケイ
素鋼板についての溶融亜鉛めっき法に関しては言及して
いない。
【０００８】本発明の目的は、含ケイ素鋼を対象とし
て、高温での耐力低下が少なく、かつ良好な溶融Ｚｎめ
っき外観を有し、耐めっき焼け性に優れた建築用耐火電
縫溶接鋼管を提供することにある。
【０００９】
【課題を解決するための手段】前記課題を解決し目的を
達成するために、本発明は以下に示す手段を用いてい
る。本発明に係る耐めっき焼け性に優れた建築用耐火電
縫溶接鋼管は、質量％で、Ｃ：0.03〜0.10％と、Ｓｉ：
0.02〜0.09％と、Ｍｎ：0.1 〜1.0 ％と、Ｍｏ：0.25〜
0.75％と、Ｖ：0.01〜0.10％と、Ａｌ：0.01〜0.1 ％
と、Ｎ：0.009 ％以下と、Ｓ：0.03％以下と、Ｐ：0.03
％以下とを含み、ＳｉとＭｏが不等式14.4Ｓｉ％＋Ｍｏ
％≦1.55 を満足し、残部がＦｅ及び不可避的不純物よ
りなり、高温での耐力低下が少なく、かつ耐めっき焼け
性に優れ良好なめっき外観を呈することを特徴とする。
【００１０】
【発明の実施の形態】本発明者は、含ケイ素鋼に亜鉛め
っきを施す場合、高温での耐力低下が少なく、かつ良好
な溶融Ｚｎめっき外観を有し、耐めっき焼け性に優れた
建築用耐火電縫溶接鋼管について鋭意研究を重ねた。
【００１１】その結果、高温強度（高温耐力）の向上に
有効なＭｏの添加により、鋼中の最適なＳｉ含有量上限
がさらに低Ｓｉ側にシフトし、さらに、Ｓｉ量が0.02％
未満では、不連続なＦｅ−Ｚｎ合金反応が起き、表層に
まだらにめっき焼け状外観不良が発生するという知見が
得られた。
【００１２】この知見に基づき、本発明者らは特定の条
件の下でＳｉとＭｏの添加量を所定のパラメータ式を満
たす最適範囲とすることにより、高温での耐力低下が少
なく、かつ良好な溶融Ｚｎめっき外観を有し、耐めっき
焼け性に優れた建築用耐火電縫溶接鋼管を見出だし、本
発明を完成した。
【００１３】すなわち、本発明は鋼組成を下記範囲に、
特にＳｉ；０．０２〜０．０９％、Ｍｏ；０．２５〜
０．７５％、ＳｉとＭｏが不等式14.4Ｓｉ％＋Ｍｏ％≦
1.55に限定することにより、高温での耐力低下が少な
く、かつ良好な溶融Ｚｎめっき外観を有し、耐めっき焼
け性に優れた建築用耐火電縫溶接鋼管を得ることができ
る。
【００１４】以下に本発明の合金の成分添加理由、成分
限定理由について説明する。
（１）成分組成範囲
Ｃは常温ならびに高温における強度を確保するために必
要な元素である。0.03％未満では高温での耐力確保に必
要な炭化物あるいは金属−炭素クラスターの析出が不十
分となる。また、0.10％を超えると常温での強度が大き
くなりすぎ建築材料に必要な低降伏応力が得られない。
従って、その範囲を0.03〜0.10％にする。 Ｍｏは鋼の
常温及び高温の降伏強度を上昇させる。特に高温におけ
る寄与が大きく、耐火性を向上させる重要な元素であ
る。0.25％未満では効果が薄いためこれを下限とする。
また、0.75％を越えて添加すると、溶融Ｚｎめっき後に
良好な外観を確保するためのＳｉ上限の制御が困難にな
ってくる上に、経済性も失われる。従って、その範囲を
0.25〜0.75％とする。
【００１５】Ｓｉは鋼板の主として常温強度の上昇に効
くが高温強度への寄与がほとんどない。また溶融Ｚｎめ
っき外観を支配する元素である。Ｓｉ量が0.02％未満で
は、不連続なＦｅ−Ｚｎ合金反応が起き、表層にまだら
にめっき焼け状外観不良が発生する。
【００１６】また、0.09％を越えてＳｉを添加すると、
Ｆｅ−Ｚｎ合金反応が過剰となり、表層にめっき焼け状
外観不良が発生する。従って、その範囲を0.02〜0.09％
とする。さらに、ＳｉとＭｏを複合添加する場合、その
含有量がパラメータ式14.4Ｓｉ％＋Ｍｏ％≦1.55を満た
す必要がある。
【００１７】Ｓｉの成分範囲は0.02〜0.09％が最適範囲
であるが、複合添加されるＭｏ含有量とともに最適範囲
は狭まり、Ｍｏ量0.7 ％では、Ｓｉ量の上限が0.059 ％
となる。図１に、鋼板の高温強度およびめっき外観に及
ぼすＳｉ量とＭｏ量の影響を示す。同図より明らかなよ
うに、14.4Ｓｉ％＋Ｍｏ％のパラメータ値が1.55超では
鋼板のめっき外観が不良となる。従って、ＳｉとＭｏの
含有量の間に14.4Ｓｉ％＋Ｍｏ％≦1.55の関係が満たさ
れるようにＳｉ，Ｍｏの含有量を限定する。
【００１８】Ｍｎは鋼の常温及び高温の降伏強度を上昇
させる。鋼の高温の降伏強度及び熱間加工性を確保する
ためには。0.1 ％以上含有させる必要がある。しかし、
1.0％を越えて含有させると、常温の降伏強度が高くな
りすぎ、溶接性が劣化する。従って、その範囲を0.1 〜
1.0 ％とする。
【００１９】ＶはＭｏの析出を促進し、高温での耐力を
上昇させるため非常に有用な元素である。しかし、0.01
％未満ではその効果が期待できず、0.10％を超えて添加
しても効果が飽和する。従って、その範囲を0.01〜0.10
％にする。
【００２０】Ａｌは脱酸材として必要であり、さらにＺ
ｎメッキ時のＦｅ−Ｚｎ合金相の成長抑制効果があるこ
とから0.01％以上添加する。0.1 ％超の添加では鋼の靭
性やメッキ性の点で好ましくないので、その上限を0.1
％にする。
【００２１】また、上記以外の元素として本発明は、
Ｐ，Ｓ，Ｎを不可避的に含有する。これら元素は高温強
度に大きな影響を与えないが、多すぎると本発明の効果
を阻害する。従って、その量を、Ｎ≦0.009 ％，Ｓ≦0.
03％，Ｐ≦0.03％に規定する。以下に本発明の実施例を
挙げ、本発明の効果を立証する。
【００２２】
【実施例】表１に本発明鋼（No.3〜8)及び比較鋼（No.
1,2,9〜16) の化学成分及びその各材料の高温強度、め
っき外観評価の結果を示す。各材料は、表１に示す化学
成分組成を有する鋼を転炉、または電気炉で溶製し、連
続鋳造法でスラブとし、ホットストリップミルにより鋼
帯として作成した。
【００２３】なお、高温強度は電縫溶接角管平行部より
試験片加工し、600 ℃で引張試験を行い、降伏点を測定
した。めっき外観評価は、Ｓｉ添加量を変化させた鋼
管、角管に対して、酸洗後、浴温430 ℃、浸漬時間1 分
の条件で溶融Ｚｎめっきを施し、目視により外観評価を
行った。その際にめっき性状が良好でめっき焼けが見ら
れないものを合格とした。○：合格、×：不合格を示
す。
【００２４】No.3〜8 の材料は本発明による鋼（本発明
例）であるが、いずれも本発明の高温強度の目標値であ
る197MPa以上を達成しており、高温強度及びめっき外観
は後述する比較材に比べて優れている。
【００２５】これらに対して、No.1,2,9の各材料はそれ
ぞれ、Ｓｉ量が本発明規定値未満となっていることか
ら、本発明例に比較してめっき外観が劣っている。特
に、No.9はＭｏ量も本発明規定値未満となっていること
から、本発明例に比較して高温強度も劣っている。
【００２６】No. 9 〜11の各材料はそれぞれ、Ｍｏ量が
本発明規定値未満となっていることから、本発明例に比
較して高温強度が劣っている。特に、No.9はＳｉ量も本
発明規定値未満であり、No.11 はＳｉ量も本発明規定値
を超えていることから、それぞれ、本発明例に比較して
めっき外観も劣っている。No.12 〜16の各材料はそれぞ
れ、14.4Ｓｉ＋Ｍｏ量が本発明規定値を超えていること
から、本発明例に比較してめっき外観が劣っている。以
上より、本発明で意図する高温強度及びめっき外観を得
るためには、Ｓｉ，Ｍｏ量を特定範囲内とすることが必
要であることが理解される。
【００２７】
【表１】【００２８】
【発明の効果】本発明は、鋼組成をＳｉ；０．０２〜
０．０９％、Ｍｏ；０．２５〜０．７５％、ＳｉとＭｏ
が不等式14.4Ｓｉ％＋Ｍｏ％≦1.55 に特定することに
より、高温での耐力低下が少なく、かつ良好な溶融Ｚｎ
めっき外観を有し、耐めっき焼け性に優れた建築用耐火
電縫溶接鋼管を提供することができ、工業上、有益な効
果をもたらすものである。Description: BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to an anti- dip coating having a small reduction in proof stress at high temperatures and having a good appearance of hot-dip Zn plating.
The present invention relates to fire-resistant electric resistance welded steel pipes for buildings, such as round pipes and square pipes, which have excellent burning properties . 2. Description of the Related Art In 1987, the fire resistance design method for buildings was reviewed, and the item of allowable temperature for steel materials at the time of fire was removed.
Along with this, a building material that has a small decrease in proof stress at high temperatures has been developed, and this building material has been used in places where the ultimate temperature at the time of fire is low, with reduced fireproof coating or with no fireproof coating. Japanese Patent Application Laid-Open No. 2-197520 discloses that a steel having a composition in which Ti or / and Nb is added to ultra-low carbon steel and a large amount of Cu is added is designed to prevent high-temperature cracking due to Cu and to have predetermined characteristics. Hot-rolling is performed under specific hot-rolling conditions so as to allow sufficient application, and in some cases, the strength is adjusted with P.
There is disclosed a method for producing a low yield ratio galvanized steel sheet for buildings having excellent fire resistance by reinforcing Ni against addition of hot cracks. [0003] The current galvanizing process generally involves immersion in a zinc bath at 440-460 ° C for about 5 minutes, whereby a continuous, dense and uniform, shiny surface is formed on the steel surface. A plating layer having a thickness suitable for the above is formed. However, in recent years, the situation has changed since a new steel type containing silicon has appeared on the market. Inevitably, with the development of these new steel grades, steel mills have developed new casting methods, mainly killing and continuous casting methods, in place of the old casting methods. The use of excellent steel grades has been increasingly widespread, with silicon-containing steel being the center of its easiest operation. As far as the galvanizing sector is concerned, the presence of silicon presently presents some difficulties in the field. Experience has shown that zinc plating of silicon-containing steel forms a gray layer with surface defects, poor adhesion, and an excessively thick plating layer. [0006] PELLERIN, J.A. HOFFMA
N, Dr. V. According to a study by LEROY et al. On the effect of silicon and phosphorus on hot-dip galvanizing of mild steel ("Lead and zinc" No. 107, published in May 1982), galvanizing steel sheets by the above-mentioned general method was used. 0.1%
<Si% + 2.5P% <0.2%, further 0.3% <Si% +
In the range of 2.5 P%, Fe-Zn alloying during immersion plating is abnormally promoted, causing poor appearance (poor luster) called "burnt plating", and the content of Si (and P) is optimal. (Si% <0.04%, Si% + 2.5 P% <
0.09%), it is shown that the Fe-Zn alloy layer is formed relatively slowly and uniformly on the steel pipe, the outermost layer of the plating is not alloyed, and a metallic luster is obtained. [0007] However, the above-mentioned Japanese Patent Application Laid-Open
The technique disclosed in Japanese Patent Application Laid-Open No. 2-197520 is not directed to silicon-containing steel having excellent mechanical properties. Also, J.I. PELERI
N, J. HOFFMAN, Dr. V. The study of LEROY et al. Does not mention a hot-dip galvanizing method for a silicon-containing steel sheet for the purpose of increasing the high-temperature strength of the steel sheet. SUMMARY OF THE INVENTION An object of the present invention is to provide a refractory welded steel pipe for architectural use in silicon-containing steel, which has a small decrease in proof stress at high temperatures, has a good hot-dip galvanized appearance, and has excellent plating burn resistance. To provide. Means for Solving the Problems In order to solve the above problems and achieve the object, the present invention uses the following means. The refractory electric resistance welded steel pipe for construction having excellent plating burn resistance according to the present invention has a mass% of C: 0.03 to 0.10% and Si:
0.02 to 0.09%, Mn: 0.1 to 1.0%, Mo: 0.25 to
0.75%, V: 0.01 to 0.10%, Al: 0.01 to 0.1%
, N: 0.009% or less, S: 0.03% or less, P: 0.03%
%, And the inequality 14.4Si% + Mo
% ≦ 1.55 was satisfied, Ri is Na Fe and unavoidable impurities balance, less strength reduction at high temperature, and resistance to plating scorch
Characterized Rukoto that Teisu good coating appearance excellent in resistance. DETAILED DESCRIPTION OF THE INVENTION The present inventor has found that when zinc-containing is applied to silicon-containing steel, the reduction in proof stress at high temperatures is small, the appearance of hot-dip Zn plating is good, and the anti-galling property is excellent. Intensive studies on the refractory welded steel pipes for architectural refractory construction. As a result, the addition of Mo, which is effective for improving the high- temperature strength (high-temperature proof stress) , shifts the upper limit of the optimum Si content in the steel further to the lower Si side, and further reduces the Si content to 0.02%.
If less than 10, it has been found that a discontinuous Fe-Zn alloy reaction occurs and mottled plating-like appearance defects occur on the surface layer. On the basis of this finding, the present inventors have determined that the addition amounts of Si and Mo satisfy specified parameter expressions under specific conditions.
By the optimum range plus, less strength reduction at high temperature, and has good melt Zn coating appearance, complete false starts, the present invention viewed excellent building fire electric resistance welding steel pipe resistance to plating burnt resistance did. That is, the present invention provides a steel composition within the following range :
In particular, Si: 0.02 to 0.09%, Mo: 0.25 to
0.75%, Si and Mo are inequalities 14.4Si% + Mo% ≦
By limiting to 1.55, it is possible to obtain a refractory welded steel pipe for building which has a small reduction in proof stress at high temperatures, has a good hot-dip galvanized appearance, and is excellent in plating burn resistance. The reasons for adding the components of the alloy of the present invention and the reasons for limiting the components will be described below. (1) The component composition range C is an element necessary for securing strength at ordinary temperature and high temperature. If it is less than 0.03%, precipitation of carbides or metal-carbon clusters necessary for securing proof stress at high temperatures becomes insufficient. On the other hand, if it exceeds 0.10%, the strength at room temperature becomes too large, and the low yield stress required for building materials cannot be obtained.
Therefore, the range is set to 0.03 to 0.10%. Mo increases the yield strength of steel at normal and high temperatures. In particular, it contributes significantly at high temperatures and is an important element for improving fire resistance. If it is less than 0.25%, the effect is weak, so this is the lower limit.
Further, if it is added in excess of 0.75%, it becomes difficult to control the upper limit of Si for securing a good appearance after hot-dip galvanizing, and the economy is lost. Therefore, the range
0.25 to 0.75%. Si is effective mainly for increasing the room temperature strength of the steel sheet, but hardly contributes to the high temperature strength. It is an element that controls the appearance of hot-dip Zn plating. If the amount of Si is less than 0.02%, a discontinuous Fe-Zn alloy reaction occurs, and a burnt plating appearance defect occurs on the surface layer. When Si is added in excess of 0.09%,
The reaction of the Fe-Zn alloy becomes excessive, and a burnt plating appearance defect occurs on the surface layer. Therefore, the range is 0.02-0.09%
And Further, when Si and Mo are added in combination, the content satisfies the parameter formula 14.4Si% + Mo% ≦ 1.55 .
Need to be The optimum range of the Si content is 0.02 to 0.09%, but the optimum range narrows with the Mo content added in a composite manner. When the Mo content is 0.7%, the upper limit of the Si content is 0.059%.
It becomes. FIG. 1 shows the influence of the amounts of Si and Mo on the high-temperature strength and the plating appearance of the steel sheet. As is clear from the figure, when the parameter value of 14.4Si% + Mo% exceeds 1.55, the plating appearance of the steel sheet becomes poor. Therefore, the contents of Si and Mo are limited so that the relationship of 14.4 Si% + Mo% ≦ 1.55 is satisfied between the contents of Si and Mo. Mn increases the normal and high temperature yield strength of steel. To ensure high temperature yield strength and hot workability of steel. Must be contained at 0.1% or more. But,
If the content exceeds 1.0%, the yield strength at room temperature becomes too high, and the weldability deteriorates. Therefore, the range is 0.1 to
1.0%. V is a very useful element for accelerating the precipitation of Mo and increasing the proof stress at high temperatures. But 0.01
%, The effect cannot be expected, and even if added over 0.10%, the effect is saturated. Therefore, the range is 0.01 to 0.10
%. Al is necessary as a deoxidizer, and Z
0.01% or more is added because it has an effect of suppressing the growth of the Fe—Zn alloy phase during n plating. Since addition of more than 0.1% is not preferable in terms of steel toughness and plating property, the upper limit is set to 0.1%.
%. Further, the present invention, as an element other than the above,
P, S, and N are inevitably contained. These elements do not significantly affect the high-temperature strength, but if they are too much, they hinder the effects of the present invention. Therefore, the amount is set to N ≦ 0.009%, S ≦ 0.
03%, P ≤ 0.03%. Hereinafter, examples of the present invention will be described to demonstrate the effects of the present invention. Examples Table 1 shows the steels of the present invention (Nos. 3 to 8) and comparative steels (No.
1, 2, 9 to 16) and the results of high-temperature strength and plating appearance evaluation of the respective chemical components are shown. Each material was prepared by melting steel having a chemical composition shown in Table 1 in a converter or an electric furnace, forming a slab by a continuous casting method, and forming a steel strip by a hot strip mill. The high-temperature strength was obtained by processing a test piece from the parallel portion of the ERW welded square tube, performing a tensile test at 600 ° C., and measuring the yield point. For the plating appearance evaluation, steel pipes and square pipes with different amounts of Si added were subjected to pickling, hot-dip Zn plating was performed under the conditions of a bath temperature of 430 ° C. and an immersion time of 1 minute, and the appearance was visually evaluated. At that time, those having good plating properties and no plating burn were judged as acceptable. ：: acceptable, ×: failed. The materials of Nos. 3 to 8 are steels according to the present invention (examples of the present invention), all of which have achieved the high temperature strength target value of 197 MPa or more of the present invention, and have high temperature strength and plating appearance. It is superior to the comparative material described below. On the other hand, each of the materials Nos. 1, 2, and 9 has an inferior plating appearance as compared with the examples of the present invention since the amounts of Si are less than the values specified in the present invention. In particular, since the Mo content of No. 9 was also less than the value specified in the present invention, the high-temperature strength was inferior to the examples of the present invention. Each of the materials of Nos. 9 to 11 is inferior in high-temperature strength as compared with the examples of the present invention since the Mo amount is less than the value specified in the present invention. In particular, No. 9 also had a Si content less than the specified value of the present invention, and No. 11 also had a Si content exceeding the specified value of the present invention. . The materials of Nos. 12 to 16 each had an inferior plating appearance as compared with the examples of the present invention since the amount of 14.4Si + Mo exceeded the specified value of the present invention. From the above, it is understood that in order to obtain the high-temperature strength and plating appearance intended in the present invention, it is necessary to set the amounts of Si and Mo within a specific range. [Table 1] According to the present invention, the steel composition is Si;
0.09%, Mo; 0.25 to 0.75%, Si and Mo
Satisfies the inequality 14.4Si% + Mo% ≦ 1.55, so that the decrease in proof stress at high temperatures is small and the molten Zn
It is possible to provide a refractory welded steel pipe for architectural use having a plated appearance and excellent plating burn resistance, and has an industrially beneficial effect.
【図面の簡単な説明】
【図１】本発明の実施の形態に係る鋼板の高温強度及び
めっき外観に及ぼすＳｉ量とＭｏ量の影響を示す図。BRIEF DESCRIPTION OF THE DRAWINGS FIG. 1 is a view showing the influence of the amounts of Si and Mo on the high-temperature strength and plating appearance of a steel sheet according to an embodiment of the present invention.
───────────────────────────────────────────────────── フロントページの続き (56)参考文献 特開 平４−228520（ＪＰ，Ａ) 特開 平６−17124（ＪＰ，Ａ) 特開 平８−158008（ＪＰ，Ａ) 特開 平５−59450（ＪＰ，Ａ) 特開 平８−85823（ＪＰ，Ａ) 特開 平10−8200（ＪＰ，Ａ) (58)調査した分野(Int.Cl.7，ＤＢ名) C22C 38/00 - 38/60 B21C 37/08 C23C 2/00 - 2/40 ──────────────────────────────────────────────────続 き Continuation of the front page (56) References JP-A-4-228520 (JP, A) JP-A-6-17124 (JP, A) JP-A-8-158008 (JP, A) JP-A-5-158008 59450 (JP, A) JP-A-8-85823 (JP, A) JP-A-10-8200 (JP, A) (58) Fields investigated (Int. Cl. 7 , DB name) C22C 38/00-38 / 60 B21C 37/08 C23C 2/00-2/40
Claims (1)
0.02〜0.09％と、Ｍｎ：0.1 〜1.0 ％と、Ｍｏ：0.25〜
0.75％と、Ｖ：0.01〜0.10％と、Ａｌ：0.01〜0.1 ％
と、Ｎ：0.009 ％以下と、Ｓ：0.03％以下と、Ｐ：0.03
％以下とを含み、ＳｉとＭｏが不等式14.4Ｓｉ％＋Ｍｏ
％≦1.55 を満足し、残部がＦｅ及び不可避的不純物よ
りなり、高温での耐力低下が少なく、かつ耐めっき焼け
性に優れ良好なめっき外観を呈することを特徴とする耐
めっき焼け性に優れた建築用耐火電縫溶接鋼管。(57) [Claims] [Claim 1] In mass% , C: 0.03 to 0.10% and Si:
0.02 to 0.09%, Mn: 0.1 to 1.0%, Mo: 0.25 to
0.75%, V: 0.01 to 0.10%, Al: 0.01 to 0.1%
, N: 0.009% or less, S: 0.03% or less, P: 0.03%
%, And the inequality 14.4Si% + Mo
% ≦ 1.55 was satisfied, Ri is Na Fe and unavoidable impurities balance, less strength reduction at high temperature, and resistance to plating scorch
Good plating appearance Teisu resistance to plating burnt excellent in building fire electric resistance welding steel pipes, characterized in Rukoto excellent sex.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP21240896A JP3533837B2 (en) | 1996-08-12 | 1996-08-12 | Refractory electric resistance welded steel pipe for construction with excellent plating resistance |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP21240896A JP3533837B2 (en) | 1996-08-12 | 1996-08-12 | Refractory electric resistance welded steel pipe for construction with excellent plating resistance |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH1053840A JPH1053840A (en) | 1998-02-24 |
| JP3533837B2 true JP3533837B2 (en) | 2004-05-31 |
Family
ID=16622100
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP21240896A Expired - Fee Related JP3533837B2 (en) | 1996-08-12 | 1996-08-12 | Refractory electric resistance welded steel pipe for construction with excellent plating resistance |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP3533837B2 (en) |
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1996
- 1996-08-12 JP JP21240896A patent/JP3533837B2/en not_active Expired - Fee Related
Also Published As
| Publication number | Publication date |
|---|---|
| JPH1053840A (en) | 1998-02-24 |
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