TWI694160B - Stainless steel material excellent in supressing slag spots generation, welded structural member and manufacturing method thereof - Google Patents

Stainless steel material excellent in supressing slag spots generation, welded structural member and manufacturing method thereof Download PDF

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TWI694160B
TWI694160B TW107118141A TW107118141A TWI694160B TW I694160 B TWI694160 B TW I694160B TW 107118141 A TW107118141 A TW 107118141A TW 107118141 A TW107118141 A TW 107118141A TW I694160 B TWI694160 B TW I694160B
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mno
stainless steel
slag
mass ratio
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TW201923108A (en
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江原靖弘
森田一成
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日商日鐵不銹鋼股份有限公司
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
    • B23K31/00—Processes relevant to this subclass, specially adapted for particular articles or purposes, but not covered by only one of the preceding main groups
    • B23K31/02—Processes relevant to this subclass, specially adapted for particular articles or purposes, but not covered by only one of the preceding main groups relating to soldering or welding
    • B23K31/027—Making tubes with soldering or welding
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
    • B23K35/00—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting
    • B23K35/22—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by the composition or nature of the material
    • B23K35/24—Selection of soldering or welding materials proper
    • B23K35/30—Selection of soldering or welding materials proper with the principal constituent melting at less than 1550 degrees C
    • B23K35/3053—Fe as the principal constituent
    • B23K35/308—Fe as the principal constituent with Cr as next major constituent
    • B23K35/3086—Fe as the principal constituent with Cr as next major constituent containing Ni or Mn
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21C—PROCESSING OF PIG-IRON, e.g. REFINING, MANUFACTURE OF WROUGHT-IRON OR STEEL; TREATMENT IN MOLTEN STATE OF FERROUS ALLOYS
    • C21C7/00—Treating molten ferrous alloys, e.g. steel, not covered by groups C21C1/00 - C21C5/00
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21C—PROCESSING OF PIG-IRON, e.g. REFINING, MANUFACTURE OF WROUGHT-IRON OR STEEL; TREATMENT IN MOLTEN STATE OF FERROUS ALLOYS
    • C21C7/00—Treating molten ferrous alloys, e.g. steel, not covered by groups C21C1/00 - C21C5/00
    • C21C7/0006—Adding metallic additives
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Treatment Of Steel In Its Molten State (AREA)

Abstract

The present invention provides a stainless steel material capable of stably and remarkably suppressing generation of slag spots in arc welding using stainless steel as a base material.
The stainless steel of the present invention, in mass %, comprising: C: 0.005 to 0.100%, Si: 0.10 to 3.00%, Mn: 0.10 to 6.50%, P: 0.001 to 0.050%, S: 0.0001 to 0.0200%, Ni: 0 to 20.00%, Cr: 10.50 to 26.00%, N: 0.005 to 0.200%, O: 0.0030 to 0.0150%, if necessary, it comprises Mo, Cu, Nb, V, Zr, W, Co, B, Ti, Al, Ca, Mg, REM (rare earth element excluding Y) and Y in a predetermined range, and it also includes balanced Fe and a chemical composition composed of inevitable impurities, the average CaO/(SiO2 + MnO + CaO) mass ratio of the oxide-based inclusions observed in the metal structure is 0.40 or less, the average CaO/MnO mass ratio is 15.0 or less.

Description

熔渣點產生抑止能力優異之不銹鋼材以及焊接構造構件及其製造方法 Stainless steel material with excellent suppression ability of slag spot generation, welded structural member and manufacturing method thereof

本發明係關於不銹鋼材，其不易產生會在電弧焊接熔珠產生之焊接缺陷的一種之所謂的「熔渣點」或「黑點」之缺陷。又，關於使用該鋼材之焊接構造構件、及其製造方法。 The present invention relates to a stainless steel material, which is not easy to cause a kind of so-called "slag point" or "black spot" defect that can occur in arc welding molten beads. In addition, it relates to a welded structural member using the steel material and a method for manufacturing the same.

將不銹鋼材使用於母材而進行電弧焊接時，有時會產生在焊接熔珠上散佈有氧化物之凝集體之所謂的「熔渣點」的缺陷。第1圖引用並例示非專利文獻1所揭載之已產生熔渣點的焊接熔珠之外觀照片。若依據非專利文獻1之記載，熔渣點係在焊接熔珠上以數mm至數cm間隔呈島狀或點狀地殘留浮出之微小熔渣。認為電弧焊接時侵入熔融池之空氣中之氧與鋼材中之微量成分的Al、Ca、Ti等活性元素反應而殘留為熔渣點，尤其在熔融池之充分氣體屏蔽困難的高速度TIG焊接中有熔渣點之產生變顯著 的傾向。 When stainless steel is used as a base material for arc welding, a defect called "slag point" in which oxide aggregates are scattered on the welding beads may sometimes occur. Figure 1 cites and exemplifies a photograph of the appearance of a welded bead with slag spots disclosed in Non-Patent Document 1. According to the description of Non-Patent Document 1, the slag spots are minute slags floating on the welding beads at island-shaped or spot-shaped intervals of several mm to several cm. It is believed that oxygen in the air that invades the molten pool during arc welding reacts with trace elements Al, Ca, Ti and other active elements in the steel to remain as slag spots, especially in high-speed TIG welding where it is difficult to fully gas shield the molten pool. The occurrence of slag spots becomes significant Propensity.

第2圖係例示藉由TIG焊接而造管而成之鋼管的焊接熔珠上所看到的熔渣點之外觀。在該鋼管所看到之長徑1.0mm以上之大小的熔渣點之在熔珠長度方向每1m之個數(以下，稱為「熔渣點產生率」)為0.7個/m。 Figure 2 illustrates the appearance of slag spots seen on the weld beads of steel pipes made by TIG welding. The number of slag spots with a length of 1.0 mm or more seen in the steel pipe per m in the longitudinal direction of the bead (hereinafter, referred to as "slag spot generating rate") was 0.7 pieces/m.

在焊接熔珠頻繁產生熔渣點時，會有例如以下之問題。 When slag spots are frequently generated by welding beads, there are problems such as the following.

(i)損及焊接熔珠部之美觀。(ii)為了除去，有時必須有熔珠表面研磨等煩雜的修整。(iii)在焊接鋼管之製造中，亦有壓下鋼管內面之焊接熔珠而降低熔珠之高度後，實施內面研磨之用途。熔渣點有亦在背熔珠側產生之情形，在此情形，壓下鋼管內面之熔珠部時熔渣點被壓進去而在熔珠之金屬面形成凹陷，在其後之研磨步驟中產生研磨未完成部分(未研磨部)。(iv)構成熔渣點之異物與熔珠之金屬表面之間有時會產生間隙腐蝕。(v)在焊接鋼管之情形，在內面熔珠上生成之熔渣點在鋼管使用中脫落，可能成為異物混入在內部流動之流體中之原因。(vi)電弧焊接時會成為熔渣點原因之異物凝集在熔融池內時，電弧會不安定，熔珠形狀容易混亂。 (i) Damage the beauty of the welded bead part. (ii) In order to remove it, it may be necessary to have troublesome finishing such as grinding of the surface of the molten beads. (iii) In the manufacture of welded steel pipes, there is also the use of carrying out internal grinding after pressing down the welding beads on the inner surface of the steel pipe to reduce the height of the beads. The slag spot may also occur on the back side of the molten bead. In this case, when the molten bead part of the inner surface of the steel pipe is pressed down, the slag spot is pressed in and a depression is formed on the metal surface of the molten bead, followed by the grinding step The unfinished part (unpolished part) is generated in the middle. (iv) Gap corrosion may sometimes occur between the foreign material constituting the slag point and the metal surface of the molten bead. (v) In the case of welded steel pipes, the slag spots generated on the inner surface of the molten beads fall off during the use of the steel pipes, which may cause foreign substances to be mixed into the fluid flowing inside. (vi) When foreign substances that cause slag spots are condensed in the molten pool during arc welding, the arc becomes unstable and the shape of the molten beads is easily disturbed.

因此，期待開發出在作為電弧焊接之母材使用時，可明顯抑制熔渣點的產生之不銹鋼材。 Therefore, it is expected to develop a stainless steel material that can significantly suppress the occurrence of slag spots when used as a base material for arc welding.

在專利文獻1、2中，揭示一種藉由將易氧化性元素之Al、Ti、Si、Ca之含量調整至最佳化的鋼組成而降低熔渣點(黑點)之生成的肥粒鐵系不銹鋼。但，依據 發明人等之調査，僅調整鋼組成，熔渣點之抑制效果有限，仍有進一步改善的空間。 Patent Documents 1 and 2 disclose a ferrite grain that reduces the generation of slag spots (black spots) by adjusting the content of oxidizable elements Al, Ti, Si, and Ca to an optimized steel composition. Department of stainless steel. However, based on According to the investigation by the inventors, only the steel composition is adjusted, and the suppression effect of the slag point is limited, and there is still room for further improvement.

在專利文獻3中，記載在被覆管用沃斯田鐵系Fe-Ni-Cr合金中，降低會成為加工龜裂起點之焊接部表面之異物。並教示附著於焊接物表面之異物係以Al、Ti、Si、Ca、Mg等之氧化物、氮化物作為主體者，且存在於母材中之非金屬夾雜物一般為高融點，故焊接時不熔融而在熔融金屬之表面浮出並凝集，凝固時，直接殘留於表面而形成凹凸(段落0035)。又，附著於焊接部表面之異物係源自於存在於母材中之非金屬夾雜物者(段落0038)。在專利文獻3所揭示之技術中，藉由除了極力降低Al、Ti、Si之量以外，還降低其他夾雜物構成元素的Ca、Mg、N及O而降低存在於母材中之夾雜物之個數，藉此，謀求在焊接金屬表面觀察到之異物的降低(段落0039)。然而，若依據發明人等之研究，只單純減少存在於不銹鋼材中之非金屬夾雜物之數量，難以穩定獲得對例如食品加工生產線或半導體製造設備所使用之焊接鋼管所要求之極少異物(熔渣點)的電弧焊接熔珠。又，大幅降低存在於不銹鋼材中之非金屬夾雜物之量，會使製鋼步驟之負荷增大，並招致鋼材成本之上昇。因此，期盼開發出可不依賴減少夾雜物之存在量的方法而謀求熔渣點之降低之新的方法。 Patent Document 3 describes that the Vostian iron-based Fe-Ni-Cr alloy for a covered tube reduces foreign matters on the surface of the welded part that will become the starting point of machining cracks. It also teaches that the foreign materials attached to the surface of the welded material are mainly composed of oxides and nitrides of Al, Ti, Si, Ca, Mg, etc., and the non-metallic inclusions in the base material are generally high melting points, so welding When it does not melt, it floats on the surface of the molten metal and aggregates. When solidified, it directly remains on the surface to form irregularities (paragraph 0035). In addition, the foreign matter adhering to the surface of the welded part originates from the non-metallic inclusions present in the base material (paragraph 0038). In the technique disclosed in Patent Document 3, by reducing the amount of Al, Ti, and Si as much as possible, and also reducing the Ca, Mg, N, and O of other inclusion constituent elements, the inclusions in the base material are reduced The number is used to reduce the foreign matter observed on the surface of the weld metal (paragraph 0039). However, according to the research of the inventors, simply reducing the amount of non-metallic inclusions present in stainless steel materials, it is difficult to stably obtain very few foreign materials required for welded steel pipes used in, for example, food processing production lines or semiconductor manufacturing equipment ( Arc welding welding beads. In addition, greatly reducing the amount of non-metallic inclusions present in the stainless steel material will increase the load on the steel-making step and incur a rise in steel cost. Therefore, it is expected to develop a new method for reducing the slag point without relying on the method for reducing the amount of inclusions.

[先前技術文獻] [Prior Technical Literature] [專利文獻] [Patent Literature]

[專利文獻1]日本特開2010-202973號公報 [Patent Document 1] Japanese Patent Application Publication No. 2010-202973

[專利文獻2]日本特開2012-36444號公報 [Patent Document 2] Japanese Unexamined Patent Publication No. 2012-36444

[專利文獻3]日本特開2014-84493號公報 [Patent Document 3] Japanese Patent Laid-Open No. 2014-84493

[非專利文獻] [Non-patent literature]

[非專利文獻1]不銹鋼協會編「不銹鋼便覧第3版」、日刊工業新聞社、1995年、p.1030-1031 [Non-Patent Document 1] "Stainless Steel Toiletry 3rd Edition" edited by the Stainless Steel Association, Nikkan Kogyo Shimbun, 1995, p. 1030-1031

在降低電弧焊接熔珠之熔渣點方面有效的焊接法可舉例如將焊線使用於電極之方法、添加熔填材之方法。使用含助焊劑之焊線亦為有效。另一方面，TIG焊接等使用非消耗性電極式之電極的電弧焊接亦被廣泛進行，不使用熔填材者亦多。 Welding methods that are effective in reducing the slag points of arc welding beads include, for example, a method of using a welding wire for an electrode and a method of adding a filler material. It is also effective to use solder wires containing flux. On the other hand, arc welding using non-expendable electrode type electrodes such as TIG welding is also widely performed, and many of them do not use fusion fillers.

本發明欲提供一種不依賴使用焊線、熔填材，即使採用非消耗性電極式之電弧焊接法時，仍可在不論沃斯田鐵系、肥粒鐵系之各種不銹鋼種穩定並顯著地抑制熔渣點之產生的技術。 The present invention is intended to provide a method that does not rely on the use of welding wires and fusion fillers. Even when the non-consumable electrode arc welding method is used, it can still be stable and significantly regardless of the variety of stainless steels in the Vostian iron system and the ferrite iron system. Technology to suppress the generation of slag spots.

發明人等詳細研究之結果，發現藉由採用除了降低存在於不銹鋼母材中之非金屬夾雜物之量以外，還控制尤其氧化物系夾雜物之組成的方法，可達成上述課題。本說明書中係揭示以下之發明。 As a result of detailed investigations by the inventors, it has been found that the above-mentioned problems can be achieved by using a method of controlling the composition of especially oxide-based inclusions in addition to reducing the amount of non-metallic inclusions present in the stainless steel base material. This specification discloses the following inventions.

〔1〕一種不銹鋼材，以質量%計，具有包含C：0.005至0.100%、Si：0.10至3.00%、Mn：0.10至6.50%、P：0.001至0.050%、S：0.0001至0.0200%、Ni：0至20.00%、Cr：10.50至26.00%、Mo：0至2.50%、Cu：0至3.50%、Nb：0至0.500%、V：0至0.500%、Zr：0至0.500%、W：0至0.500%、Co：0至0.500%、B：0至0.020%、N：0.005至0.200%、Ti：0至0.050%、Al：0至0.100%、Ca：0至0.0010%、Mg：0至0.0010%、REM(除了Y以外之稀土元素)：0至0.050%、Y：0至0.050%、O：0.0030至0.0150%、殘部Fe及不可避免的雜質之化學組成，且存在含有Mn之氧化物系夾雜物，在氧化物系夾雜物中之Si、Mn及Ca之含量分別換算成SiO2、MnO及CaO之質量比例時之夾雜物組成中，在金屬組織中所觀察到之氧化物系夾雜物之平均CaO/(SiO2+MnO+CaO)質量比為0.40以下，平均CaO/MnO質量比為15.0以下。 [1] A stainless steel material having, by mass %, C: 0.005 to 0.100%, Si: 0.10 to 3.00%, Mn: 0.10 to 6.50%, P: 0.001 to 0.050%, S: 0.0001 to 0.0200%, Ni: 0 to 20.00%, Cr: 10.50 to 26.00%, Mo: 0 to 2.50%, Cu: 0 to 3.50%, Nb: 0 to 0.500%, V: 0 to 0.500%, Zr: 0 to 0.500%, W : 0 to 0.500%, Co: 0 to 0.500%, B: 0 to 0.020%, N: 0.005 to 0.200%, Ti: 0 to 0.050%, Al: 0 to 0.100%, Ca: 0 to 0.0010%, Mg: 0 to 0.0010%, REM (rare earth elements other than Y): 0 to 0.050%, Y: 0 to 0.050%, O: 0.0030 to 0.0150%, chemical composition of residual Fe and inevitable impurities, and the presence of Mn Oxide-based inclusions, oxides observed in the metal structure in the composition of inclusions when the contents of Si, Mn, and Ca in the oxide-based inclusions are converted to the mass ratio of SiO 2 , MnO, and CaO, respectively The average CaO/(SiO 2 +MnO+CaO) mass ratio of the inclusions is 0.40 or less, and the average CaO/MnO mass ratio is 15.0 or less.

〔2〕一種電弧焊接用母材，係包含上述〔1〕所述之不銹鋼材。 [2] A base material for arc welding comprising the stainless steel material described in [1] above.

〔3〕一種電弧焊接造管用鋼板母材，係包含上述〔1〕所述之不銹鋼材。。 [3] A steel plate base material for arc welding pipe forming, comprising the stainless steel material described in [1] above. .

〔4〕一種電弧焊接構造構件，係將上述〔1〕所述之不銹鋼材使用於母材中。 [4] An arc welding structural member using the stainless steel material described in [1] above as a base material.

〔5〕一種電弧焊接鋼管，係將上述〔1〕所述之不銹鋼材使用於母材中。 [5] An arc-welded steel pipe using the stainless steel material described in [1] above as a base material.

〔6〕一種焊接構造構件之製造方法，係將上述〔1〕 所述之不銹鋼材使用於母材中，且不添加熔填材而進行非消耗性電極式之電弧焊接。 [6] A method of manufacturing a welded structural member, using the above [1] The above-mentioned stainless steel material is used in the base material, and non-consumable electrode type arc welding is performed without adding a filler material.

〔7〕一種焊接鋼管之製造方法，係將上述〔1〕所述之不銹鋼材之鋼板使用於母材中，且不添加熔填材而以非消耗性電極式之電弧焊接形成焊接鋼管。 [7] A method of manufacturing a welded steel pipe, which uses the steel sheet of the stainless steel material described in [1] above as a base material, and forms a welded steel pipe by non-consumable electrode arc welding without adding a filler material.

在此，上述各鋼成分之含量為存在於鋼中之該元素之全部含量。因此，一部份以氧化物形式存在之金屬元素或氧之含量係包含以氧化物形式存在之量。氧化物系夾雜物之平均CaO/(SiO2+MnO+CaO)質量比、平均CaO/MnO質量比可如以下方式求取。電弧焊接構造構件係具有藉由電弧焊接所形成之焊接部的構件。同樣地，電弧焊接鋼管係具有藉由電弧焊接所形成之焊接部的鋼管。此等之焊接部可設為「無添加熔填材之焊接部」(亦即，不添加熔填材所形成之焊接部)。 Here, the content of each steel component mentioned above is the total content of the element present in the steel. Therefore, a part of the metal element or oxygen content in the form of oxide includes the amount in the form of oxide. The average CaO/(SiO 2 +MnO+CaO) mass ratio and the average CaO/MnO mass ratio of oxide-based inclusions can be obtained as follows. The arc welding structural member is a member having a welding portion formed by arc welding. Similarly, the arc-welded steel pipe is a steel pipe having a welded portion formed by arc welding. These welded parts can be set as "welded parts without added filler material" (that is, welded parts formed without added filler material).

〔平均CaO/(SiO2+MnO+CaO)質量比、平均CaO/MnO質量比之求取方式〕 [Method for obtaining the average CaO/(SiO 2 +MnO+CaO) mass ratio and average CaO/MnO mass ratio]

針對鋼材之截面進行SEM觀察，從存在於截面內之氧化物系夾雜物之粒子中隨機選擇30個以上之粒子並藉由EDX(能量分散型X射線分析)分析組成。針對各個粒子，將Si、Mn、Ca、Al、Mg、Ti、Cr及Fe之含有率分別換算成氧化物SiO2、MnO、CaO、Al2O3、MgO、TiO2、Cr2O3及FeO之質量比例，此等8種類之氧化物中SiO2、MnO及CaO所佔之質量比例分別設為該粒子之SiO2含量(質量 %)、MnO含量(質量%)及CaO含量(質量%)。藉由將各個粒子之SiO2含量、MnO含量及CaO含量分別相加平均，而算出針對全測定粒子之SiO2、MnO及CaO之平均含量(質量%)。在下述(1)式之各氧化物之化學式之處代入該氧化物之前述平均含量(質量%)之值，藉此，定出平均CaO/(SiO2+MnO+CaO)質量比。同樣地，在下述(2)式之各氧化物之化學式之處代入該氧化物之前述平均含量(質量%)之值，藉此，定出平均CaO/MnO質量比。 SEM observation was performed on the cross section of the steel material, and more than 30 particles were randomly selected from the particles of the oxide-based inclusions present in the cross section and analyzed by EDX (energy dispersive X-ray analysis). For each particle, the contents of Si, Mn, Ca, Al, Mg, Ti, Cr, and Fe are converted into oxides SiO 2 , MnO, CaO, Al 2 O 3 , MgO, TiO 2 , Cr 2 O 3 and The mass ratio of FeO, the mass ratio of SiO 2 , MnO and CaO in these 8 kinds of oxides is set as the SiO 2 content (mass %), MnO content (mass %) and CaO content (mass %) of the particles ). The average content (mass %) of SiO 2 , MnO, and CaO for all the measured particles is calculated by adding and averaging the SiO 2 content, MnO content, and CaO content of each particle, respectively. The value of the aforementioned average content (mass %) of the oxide is substituted for the chemical formula of each oxide of the following formula (1), thereby determining the average CaO/(SiO 2 +MnO+CaO) mass ratio. Similarly, the value of the aforementioned average content (mass %) of the oxide is substituted into the chemical formula of each oxide of the following formula (2), thereby determining the average CaO/MnO mass ratio.

CaO/(SiO2+MnO+CaO)...(1) CaO/(SiO 2 +MnO+CaO)...(1)

CaO/MnO...(2) CaO/MnO...(2)

若依據本發明，在不銹鋼材之電弧焊接中可穩定並明顯地抑制熔渣點之產生。該技術係不論沃斯田鐵系、肥粒鐵系而可應用於各種不銹鋼種，且特別以不添加熔填材而進行之TIG焊接，效果較大。 According to the present invention, the generation of slag spots can be stably and significantly suppressed in the arc welding of stainless steel materials. This technology is applicable to various stainless steel types regardless of the Vostian iron system and the ferrite iron system, and it is particularly effective in TIG welding without adding filler material.

第1圖係引用非專利文獻1所揭載之已產生熔渣點的焊接熔珠之外觀照片。 Figure 1 is a photograph of the appearance of a welded bead that has generated slag spots as disclosed in Non-Patent Document 1.

第2圖係藉由TIG焊接而造管而成之鋼管之焊接熔珠上所看到的熔渣點之外觀照片。 Figure 2 is a photograph of the appearance of the slag point seen on the welding beads of a steel pipe made by TIG welding.

第3圖係表示氧化物系夾雜物之平均CaO/(SiO2+MnO+CaO)質量比與熔渣點產生率之關係的圖表。 Figure 3 is a graph showing the relationship between the average CaO/(SiO 2 +MnO+CaO) mass ratio of oxide-based inclusions and the slag point generation rate.

第4圖係表示氧化物系夾雜物之平均CaO/MnO質量 比與熔渣點產生率之關係的圖表。 Figure 4 shows the average CaO/MnO mass of oxide-based inclusions A graph showing the relationship between the ratio and the slag point generation rate.

第5圖係放大表示第4圖之平均CaO/MnO質量比低之區域的圖表。 Fig. 5 is an enlarged view of the area where the average CaO/MnO mass ratio in Fig. 4 is low.

第6圖係表示鋼材中之全部氧含量與氧化物系夾雜物之平均CaO/MnO質量比的關係之圖表。 Figure 6 is a graph showing the relationship between the total oxygen content in steel and the average CaO/MnO mass ratio of oxide-based inclusions.

第7圖係放大表示第6圖之平均CaO/MnO質量比低之區域的圖表。 FIG. 7 is an enlarged view of the area where the average CaO/MnO mass ratio in FIG. 6 is low.

第8圖係表示鋼材中之全部氧含量與熔渣點產生率之關係的圖表。 Figure 8 is a graph showing the relationship between the total oxygen content in steel and the slag point generation rate.

第9圖係表示精煉時之熔渣鹼度與熔渣點產生率之關係的圖表。 Figure 9 is a graph showing the relationship between the slag basicity during refining and the slag point generation rate.

〔鋼之成分組成〕 [The composition of steel]

在本發明中，不論沃斯田鐵系、肥粒鐵系，各種鋼種皆成為應用對象。依據發明人等之研究，可獲得在以下之組成範圍中控制後述之夾雜物組成所致之抑制熔渣點之效果。 In the present invention, regardless of the Vostian iron system and the ferrite grain iron system, various steel types are applied. According to the studies of the inventors, the effect of suppressing the slag point due to the inclusion composition described below is controlled within the following composition range.

以質量%計，C：0.005至0.100%、Si：0.10至3.00%、Mn：0.10至6.50%、P：0.001至0.050%、S：0.0001至0.0200%、Ni：0至20.00%、Cr：10.50至26.00%、Mo：0至2.50%、Cu：0至3.50%、Nb：0至0.500%、V：0至0.500%、Zr：0至0.500%、W：0至0.500%、Co：0至0.500%、B：0至0.020%、N：0.005至0.200%、Ti：0至0.050%、Al：0至0.100%、Ca：0至0.0010%、Mg：0至0.0010%、REM(除 了Y以外之稀土元素)：0至0.050%、Y：0至0.050%、O：0.0030至0.0150%、殘部Fe及不可避免的雜質。 In terms of mass %, C: 0.005 to 0.100%, Si: 0.10 to 3.00%, Mn: 0.10 to 6.50%, P: 0.001 to 0.050%, S: 0.0001 to 0.0200%, Ni: 0 to 20.00%, Cr: 10.50 To 26.00%, Mo: 0 to 2.50%, Cu: 0 to 3.50%, Nb: 0 to 0.500%, V: 0 to 0.500%, Zr: 0 to 0.500%, W: 0 to 0.500%, Co: 0 to 0.500%, B: 0 to 0.020%, N: 0.005 to 0.200%, Ti: 0 to 0.050%, Al: 0 to 0.100%, Ca: 0 to 0.0010%, Mg: 0 to 0.0010%, REM (except Rare earth elements other than Y): 0 to 0.050%, Y: 0 to 0.050%, O: 0.0030 to 0.0150%, residual Fe and inevitable impurities.

鋼材中之P、S之含量一般以低者為較佳，但過度的脫磷、脫硫會提高製鋼之負荷，變得不經濟，故在此以P、S含量為上述範圍之鋼為對象。Ni、Mo、Cu、Nb、V、Zr、W、Co、B、Ti、Al、Ca、Mg、REM(除了Y以外之稀土元素)，Y為任意含有元素。此等係為了改善鋼材之熱加工性、各種特性而適當地添加於不銹鋼之一般的元素，若為上述範圍內之含量，只要氧化物系夾雜物之平均CaO/MnO質量比控制在後述之預定範圍，則並非阻礙電弧焊接熔珠之熔渣點抑制效果者。有關Ti、Al，含量為過量時，會有對夾雜物組成造成不良影響之情形，並可能成為熔渣點之產生原因，故Ti限制在0.050%以下，Al限制在0.100%以下。以Ti成為未達0.010%，Al成為0.007%以下之含量範圍之方式調整成分為更佳。欲充分降低Al含量，以在精煉中進行Si脫氧為較佳。 The content of P and S in steel is generally lower, but excessive dephosphorization and desulfurization will increase the load of steel making and become uneconomical, so the steel with P and S content in the above range is targeted here . Ni, Mo, Cu, Nb, V, Zr, W, Co, B, Ti, Al, Ca, Mg, REM (rare earth elements other than Y), Y is an arbitrary element. These are general elements that are appropriately added to stainless steel in order to improve the hot workability and various characteristics of the steel. If the content is within the above range, as long as the average CaO/MnO mass ratio of the oxide-based inclusions is controlled to be described later The range does not hinder the slag point suppression effect of arc welding beads. Regarding Ti and Al, when the content is excessive, it may cause adverse effects on the composition of inclusions, and may be the cause of the slag point. Therefore, Ti is limited to 0.050% or less, and Al is limited to 0.100% or less. It is better to adjust the composition so that Ti becomes less than 0.010% and Al becomes 0.007% or less. To sufficiently reduce the Al content, Si deoxidation during refining is preferred.

〔氧化物系夾雜物之組成〕 [Composition of oxide-based inclusions]

將不銹鋼材使用於母材之電弧焊接熔珠產生的熔渣點之產生的主因，認為是以下之模式。 The main reason for the occurrence of the slag point generated by the arc welding bead of the stainless steel material for the base material is considered to be the following mode.

(模式1)母材中之易氧化性元素(Al、Ca、Ti等)在氣體屏蔽不充分之處形成氧化物而殘留於熔珠上。 (Mode 1) The easily oxidizable elements (Al, Ca, Ti, etc.) in the base material form oxides where gas shielding is insufficient, and remain on the beads.

(模式2)存在於母材中之解離溫度高的非金屬夾雜物隨著電弧之掃描而凝集浮起，凝集粒子變大到某種程度時， 從電弧之掃描被留下而殘留於熔珠上。 (Mode 2) Non-metallic inclusions with a high dissociation temperature existing in the base material agglomerate and float with the scanning of the arc, and the aggregated particles become large to some extent, The scan from the arc is left behind and remains on the molten beads.

若依據發明人等之研究，即使在充分進行氣體屏蔽之情況下仍會產生熔渣點，故為了穩定並明顯抑制熔渣點之產生，必須克服上述模式2之產生主因。有關上述模式1之產生主因，可藉由在母材之鋼組成中將易氧化性元素等之含量限制於上述之範圍而解決。 According to the research of the inventors, even if the gas shielding is sufficiently performed, slag spots will still be generated. Therefore, in order to stabilize and significantly suppress the generation of slag spots, the main cause of the above mode 2 must be overcome. The main cause of the above mode 1 can be solved by limiting the content of easily oxidizable elements and the like to the above range in the steel composition of the base material.

就上述模式2之產生主因的對策而言，母材中之夾雜物控制很重要。非金屬夾雜物之中，成為熔渣點之原因者係解離溫度高的氧化物系夾雜物。具有上述鋼組成之不銹鋼之情形，存在於鋼材中之氧化物系夾雜物之代表性構成成分可舉例如SiO2、MnO、CaO、Al2O3、MgO等。此等之中，CaO因解離溫度高，故焊接時仍不被還原而持續以氧化物存在。其在因電弧之熱而熔融的金屬之中若進行凝集合體，冷卻後會以熔渣點之形式出現。另一方面，MnO、SiO2因解離溫度比較低，故構成氧化物之Mn、Si在焊接時被還原而成為金屬，在熔融金屬中容易溶解。因此，MnO、SiO2難以成為熔渣點之產生主因。 Regarding the countermeasures for the main cause of the above mode 2, the control of inclusions in the base material is important. Among non-metallic inclusions, oxide-based inclusions having a high dissociation temperature are responsible for the slag point. In the case of stainless steel having the above-mentioned steel composition, representative constituent components of oxide-based inclusions present in the steel material include, for example, SiO 2 , MnO, CaO, Al 2 O 3 , and MgO. Among these, CaO has a high dissociation temperature, so it is not reduced during welding and continues to exist as an oxide. If it aggregates among the metal melted by the heat of the arc, it will appear as slag spots after cooling. On the other hand, since the dissociation temperature of MnO and SiO 2 is relatively low, the Mn and Si constituting the oxide are reduced during welding to become a metal, and are easily dissolved in the molten metal. Therefore, it is difficult for MnO and SiO 2 to be the main causes of slag spots.

發明人等係針對在上述之鋼組成範圍中的各種不銹鋼種，詳細研究在鋼材中所含之氧化物系夾雜物之組成。其結果，可知存在於一般的不銹鋼材中之氧化物系夾雜物大多係SiO2及CaO之含量多的型式者。又，亦可確認藉由改變精煉條件，能夠進行減少夾雜物之CaO含量，取而代之地增加MnO含量之夾雜物的組成控制。再者，得知在夾雜物組成中，增加與SiO2、CaO共存之MnO之含 量時，雖然CaO存在，但可明顯抑制熔渣點之產生。在下述中，將SiO2及CaO之含量多之一般型式之氧化物系夾雜物為了方便而稱為「SiO2-CaO型式」，並將藉由夾雜物之組成控制而謀求Ca濃度之減少及Mn濃度之增加的型式之氧化物系夾雜物為了方便而稱為「SiO2-MnO-CaO型式」。 The inventors have studied in detail the composition of oxide-based inclusions contained in steel materials for various types of stainless steel in the above-mentioned steel composition range. As a result, it can be seen that most of the oxide-based inclusions present in general stainless steel materials are types with a large content of SiO 2 and CaO. In addition, it can also be confirmed that by changing the refining conditions, the composition control of the inclusions that can reduce the CaO content of the inclusions and instead increase the MnO content can be performed. Furthermore, it was found that when the content of MnO coexisting with SiO 2 and CaO is increased in the inclusion composition, although CaO is present, the generation of slag spots can be significantly suppressed. In the following, the general type of oxide-based inclusions with a large content of SiO 2 and CaO is called “SiO 2 -CaO type” for convenience, and the Ca concentration will be reduced by controlling the composition of the inclusions and The oxide-type inclusions of the type with increased Mn concentration are called "SiO 2 -MnO-CaO type" for convenience.

金屬氧化物在溫度上昇時，一般會解離成金屬與氧。例如若在埃林漢姆圖(Ellingham diagram)中對假設氧分壓為10-12atm時之解離溫度進行估計，則SiO2：約1530℃、MnO：約1380℃、CaO：約2100℃、Al2O3：約2020℃。將SiO2-CaO型式之夾雜物盡可能地改變成SiO2-MnO-CaO型式，亦即將夾雜物之組成設為SiO2-MnO-CaO型式相對地優勢，有利於熔渣點之抑制。又，Al2O3之解離溫度高，但在被調整成為上述鋼組成之鋼材中，因Al2O3之存在量少，故難以成為熔渣點之產生主因。 Metal oxides generally dissociate into metals and oxygen when the temperature rises. For example, if the dissociation temperature at an oxygen partial pressure of 10 -12 atm is estimated in the Ellingham diagram, then SiO 2 : about 1530°C, MnO: about 1380°C, CaO: about 2100°C, Al 2 O 3 : about 2020°C. The SiO 2 -CaO type of inclusions as far as possible changes to the SiO 2 -MnO-CaO type, i.e. the composition of inclusions is set to SiO 2 -MnO-CaO type opposite to advantage, it is advantageous in suppressing the slag point. In addition, the dissociation temperature of Al 2 O 3 is high, but in the steel material adjusted to the above-mentioned steel composition, since the amount of Al 2 O 3 is small, it is difficult to be the main cause of slag spots.

就定量地表示夾雜物組成中之SiO2-CaO型式與SiO2-MnO-CaO型式之相對優勢性之指標而言，在本發明中，係採用「平均CaO/MnO質量比」。該值愈小，可評估為SiO2-MnO-CaO型式相對地優勢之夾雜物組成，對抑制熔渣點之產生為有利。平均CaO/MnO質量比可由上述之方法求取。詳細的研究之結果，在鋼組成被調整至上述之範圍的不銹鋼中，平均CaO/MnO質量比為15.0以下時，相較於以往之不銹鋼材，可看出熔渣點之顯著的減少效果。平均CaO/MnO質量比為10.0以下係更佳，亦可管 控至6.0以下。 It can be expressed quantitatively in the composition of inclusions and the SiO 2 -CaO type indication of the relative advantage of the SiO 2 -MnO-CaO type of, in the present invention, a system using "average CaO / MnO mass ratio." The smaller the value, the more favorable the inclusion composition of the SiO 2 -MnO-CaO type, which is beneficial to suppress the generation of slag spots. The average CaO/MnO mass ratio can be obtained by the method described above. As a result of detailed studies, in stainless steels with the steel composition adjusted to the above range, when the average CaO/MnO mass ratio is 15.0 or less, a significant reduction effect of slag points can be seen compared to conventional stainless steel materials . The average CaO/MnO mass ratio of 10.0 or less is better, and it can also be controlled to 6.0 or less.

另一方面，即使在氧化物系夾雜物中之MnO含量高時，若CaO含量過高，則無法充分獲得熔渣點之產生抑制效果。研究之結果，以設為平均CaO/(SiO2+MnO+CaO)質量比為0.40以下之夾雜物組成為較佳。平均CaO/(SiO2+MnO+CaO)質量比可由上述之方法求得。 On the other hand, even if the content of MnO in the oxide-based inclusions is high, if the content of CaO is too high, the effect of suppressing the generation of slag spots cannot be sufficiently obtained. As a result of the investigation, the composition of inclusions with an average CaO/(SiO 2 +MnO+CaO) mass ratio of 0.40 or less is preferred. The average CaO/(SiO 2 +MnO+CaO) mass ratio can be obtained by the method described above.

〔夾雜物之組成控制〕 [Control of composition of inclusions]

氧化物系夾雜物之平均CaO/(SiO2+MnO+CaO)質量比、及平均CaO/MnO質量比經最佳化之上述不銹鋼材，可利用一般的不銹鋼之熔製設備而製造。代表性者可舉例如VOD製程及AOD製程。不論哪一種，首先，實施將氧吹入含Cr熔鐵中之脫碳，以常用方法製造在熱熔液面上具有含有Cr氧化物之熔渣的熔鋼(C含量為例如0.20%以下)。該階段之熔鋼係已結束吹入氧之脫碳的熔鋼，故易氧化性元素Si、Ti、Al、Ca、Mg等從熔鋼中被氧化而除去。亦即，在熔鋼中幾乎不存在Si、Ti、Al、Ca、Mg。又，熔鋼中大量地含有之Cr之一部亦會被氧化，以Cr氧化物形式在熔鋼之熱熔液面上形成熔渣。另一方面，在熔鋼中為了脫碳而吹入之氧會大量溶存。因此，必須在鑄造前進行脫氧。並非使用Al而是使用FeSi合金作為脫氧劑，進行最終的成分調整。 The above-mentioned stainless steel material in which the average CaO/(SiO 2 +MnO+CaO) mass ratio and the average CaO/MnO mass ratio of the oxide-based inclusions are optimized can be manufactured using general stainless steel melting equipment. Representative examples include the VOD process and the AOD process. In either case, first, decarburization by blowing oxygen into molten iron containing Cr is carried out, and a molten steel having a molten slag containing Cr oxide on the surface of the hot melt is manufactured by a common method (C content is, for example, 0.20% or less) . The molten steel at this stage is a decarburized molten steel that has been blown with oxygen, so the easily oxidizable elements Si, Ti, Al, Ca, Mg, etc. are oxidized and removed from the molten steel. That is, Si, Ti, Al, Ca, and Mg hardly exist in molten steel. In addition, a part of Cr contained in a large amount in molten steel is also oxidized, and slag is formed on the hot melt surface of the molten steel in the form of Cr oxide. On the other hand, the oxygen blown in molten steel for decarburization will be dissolved in a large amount. Therefore, deoxidation must be performed before casting. Instead of using Al, FeSi alloy is used as a deoxidizer to adjust the final composition.

為了一邊將氧化物系夾雜物之平均CaO/(SiO2+MnO+CaO)質量比維持在0.40以下一邊將平均 CaO/MnO質量比充分降低，可知在進行脫氧及最終的成分調整時，以滿足例如以下3點之方式進行精煉為極有效。 In order to sufficiently reduce the average CaO/MnO mass ratio while maintaining the average CaO/(SiO 2 +MnO+CaO) mass ratio of oxide-based inclusions below 0.40, it is known that when deoxidation and final component adjustment are performed, For example, the following three points are very effective for refining.

(1)以使鋼中之氧含量(亦包含存以氧化物形式存在之氧的全部氧含量)成為0.0030%(30ppm)以上之方式進行精煉。氧含量低於0.0030%時，使平均CaO/MnO質量比穩定且設為15.0以下之精煉變困難。欲使平均CaO/MnO質量比大幅降低至10.0以下、或6.0以下為止時，較佳係將氧含量調整成為0.0040%(40ppm)以上。但，氧含量過多時，會大量生成Cr氧化物含量多之夾雜物，成為引起製品品質降低的主因。氧含量限制於0.0150%(150ppm)以下，以設為0.0100%(100ppm)以下為更佳。亦可管控至0.0060%(60ppm)以下。 (1) Refining is performed so that the oxygen content in steel (including all oxygen content in the form of oxides) is 0.0030% (30 ppm) or more. When the oxygen content is less than 0.0030%, it becomes difficult to stabilize the average CaO/MnO mass ratio and set it to 15.0 or less. When the average CaO/MnO mass ratio is to be significantly reduced to 10.0 or less or 6.0 or less, it is preferable to adjust the oxygen content to 0.0040% (40 ppm) or more. However, when the oxygen content is too large, inclusions with a large amount of Cr oxide will be generated in large quantities, which will be the main cause of the degradation of product quality. The oxygen content is limited to 0.0150% (150 ppm) or less, preferably 0.0100% (100 ppm) or less. It can also be controlled below 0.0060% (60ppm).

(2)使用Ca含量為例如0.20%以下之高純度FeSi合金而進行Si脫氧。 (2) Deoxidation of Si is performed using a high-purity FeSi alloy with a Ca content of, for example, 0.20% or less.

(3)將熔渣鹼度CaO/SiO2調整為1.20至1.60之範圍。 (3) The slag basicity CaO/SiO 2 is adjusted to the range of 1.20 to 1.60.

[實施例][Example]

利用VOD製程，熔製表1所示之不銹鋼，獲得連續鑄造厚板(slab)。在最終的精煉過程中，改變鋼中之全部氧含量、脫氧劑之FeSi合金種類、及熔渣鹼度(CaO/SiO2)之條件，嘗試控制夾雜物。在表2中表示各別之條件。表2中之氧含量係再揭示表1之值。脫氧劑之FeSi合金係使用雜質量少之高純度品及通常品。高純度品係Ca含量降低至0.20質量%以下者。通常品之Ca含量為約0.5 至1.5質量%。熔渣鹼度係分析從熔渣採取出之試樣而求出。 Using the VOD process, the stainless steel shown in Table 1 was melted to obtain a continuous casting slab. In the final refining process, change the total oxygen content in the steel, the type of FeSi alloy of the deoxidizer, and the conditions of the slag basicity (CaO/SiO 2 ) to try to control the inclusions. Table 2 shows the individual conditions. The oxygen content in Table 2 reveals the values in Table 1 again. The FeSi alloy of the deoxidizer uses high-purity products and ordinary products with few impurities. The Ca content of the high-purity strain is reduced to less than 0.20% by mass. The Ca content of ordinary products is about 0.5 to 1.5% by mass. The slag basicity is obtained by analyzing the sample taken from the slag.

使用所獲得之連續鑄造厚板，以包含熱軋、冷軋之步驟獲得板厚0.5至1.5mm之冷軋退火鋼板。對於平行於該冷軋退火鋼板之軋延方向及板厚方向之截面(L截面)進行SEM(掃描型電子顯微鏡)觀察，以附屬於SEM之EDX(能量分散型X射線分析)進行氧化物系夾雜物之組成分析。根據隨機選擇之30個氧化物系夾雜物之測定值，依據前述之「平均CaO/(SiO2+MnO+CaO)質量比、平均CaO/MnO質量比之求取方式」求出平均CaO/(SiO2+MnO+CaO)質量比及平均CaO/MnO質量比。將結果表示於表2中。 Using the obtained continuous cast thick plate, a cold-rolled annealed steel plate with a plate thickness of 0.5 to 1.5 mm is obtained in steps including hot rolling and cold rolling. The cross section (L cross section) parallel to the rolling direction and the thickness direction of the cold rolled annealed steel sheet was observed by SEM (scanning electron microscope), and the oxide system was performed by EDX (energy dispersive X-ray analysis) attached to the SEM Analysis of the composition of inclusions. According to the measured values of 30 oxide-based inclusions randomly selected, the average CaO/( is calculated according to the aforementioned "method of obtaining the average CaO/(SiO 2 +MnO+CaO) mass ratio and average CaO/MnO mass ratio" SiO 2 +MnO+CaO) mass ratio and average CaO/MnO mass ratio. The results are shown in Table 2.

使用各冷軋退火鋼板作為原材料，以TIG焊接並以通常之條件製造焊接鋼管。管之外徑為25至51mm之範圍。焊接時，不添加熔填材。從所得之鋼管製品隨機抽出試樣，對於連續之長度50m以上的焊接熔珠調查熔渣點之產生。計算長徑(粒子最長之部分的直徑)為1.0mm以上之熔渣點之數量，以每1m之上述熔渣點的產生個數作為熔渣點產生率(個/m)。若上述大小之熔渣點產生率為0.30個/m以下，可評價為較以往更大幅地抑制熔渣點之產生。因此，將熔渣點產生率為0.30個/m以下者判定為合格。 將此等之結果表示於表2中。 Using each cold-rolled annealed steel sheet as a raw material, TIG welding is used to manufacture welded steel pipes under normal conditions. The outer diameter of the tube is in the range of 25 to 51 mm. When welding, no filler material is added. Samples were randomly taken from the obtained steel pipe products, and the occurrence of slag points was investigated for continuous welding beads with a length of more than 50m. Calculate the number of slag spots whose long diameter (the diameter of the longest part of the particles) is 1.0 mm or more, and take the number of slag spots generated per 1 m as the rate of slag spot generation (pieces/m). If the generation rate of the slag spots of the above size is 0.30 pieces/m or less, it can be evaluated that the generation of slag spots is more greatly suppressed than in the past. Therefore, those with a slag point generation rate of 0.30 pieces/m or less were judged as passing. The results are shown in Table 2.

Figure 107118141-A0202-12-0015-1
Figure 107118141-A0202-12-0015-1

Figure 107118141-A0202-12-0016-2
Figure 107118141-A0202-12-0016-2

鋼組成滿足本發明規定範圍，且氧化物系夾雜物之平均CaO/(SiO2+MnO+CaO)質量比及平均CaO/MnO質量比被控制在本發明規定範圍之本發明例係熔渣點之產生非常少。 The steel composition satisfies the prescribed range of the present invention, and the average CaO/(SiO 2 +MnO+CaO) mass ratio and the average CaO/MnO mass ratio of the oxide-based inclusions are controlled within the prescribed range of the present invention. Very little.

相對於此，屬於比較例之No.21至23係精煉時之熔渣鹼度高，故氧化物系夾雜物之平均CaO/MnO質量比變高，熔渣點之產生較多。No.24至26係鋼中之全部氧含量過低，且精煉時之熔渣鹼度高，故氧化物系夾雜物之平均CaO/MnO質量比明顯較其他例更高，無法獲得熔渣點之抑制效果。No.27至30係使用「通常品」作為屬於脫氧劑之FeSi合金，故無法做到所期望之夾雜物控制，而氧化物系夾雜物之平均CaO/MnO質量比變高，熔渣點之產生較多。 In contrast, Nos. 21 to 23 belonging to the comparative examples have high slag basicity during refining, so the average CaO/MnO mass ratio of oxide-based inclusions becomes high, and slag spots are generated more frequently. The total oxygen content in No.24 to 26 series steel is too low, and the slag basicity during refining is high, so the average CaO/MnO quality ratio of oxide-based inclusions is significantly higher than other examples, and the slag point cannot be obtained The inhibitory effect. Nos. 27 to 30 use "ordinary products" as FeSi alloys that are deoxidizers, so the desired inclusion control cannot be achieved, and the average CaO/MnO mass ratio of oxide-based inclusions becomes high, and the slag point Produce more.

第3圖中表示有關各例之氧化物系夾雜物的平均CaO/(SiO2+MnO+CaO)質量比與熔渣點產生率之關係。黑色圓點係使用「高純度品」作為屬於脫氧劑之FeSi合金的例，白色圓點係使用「通常品」之例(以下之第4圖至第9圖中亦同)。又，在第4圖、第5圖中表示有關各例之氧化物系夾雜物的平均CaO/MnO質量比與熔渣點產生率之關係。第5圖係放大表示第4圖之平均CaO/MnO質量比低之區域。可知藉由將氧化物系夾雜物之平均CaO/(SiO2+MnO+CaO)質量比控制於0.40以下、且將平均CaO/MnO質量比控制於15.0以下，而抑制熔渣點產生的效果顯著提升。 Fig. 3 shows the relationship between the average CaO/(SiO 2 +MnO+CaO) mass ratio of the oxide-based inclusions of each example and the slag point generation rate. The black dots use the "high purity product" as an example of the FeSi alloy that belongs to the deoxidizer, and the white dot use the "normal product" (the same applies to the following Figures 4 to 9). In addition, FIG. 4 and FIG. 5 show the relationship between the average CaO/MnO mass ratio of the oxide-based inclusions of each example and the slag point generation rate. FIG. 5 is an enlarged view showing the area where the average CaO/MnO mass ratio in FIG. 4 is low. It can be seen that by controlling the average CaO/(SiO 2 +MnO+CaO) mass ratio of oxide-based inclusions to 0.40 or less and the average CaO/MnO mass ratio to 15.0 or less, the effect of suppressing the generation of slag spots is remarkable Promote.

第6圖、第7圖中表示有關各例之鋼材中的全部氧含量與氧化物系夾雜物之平均CaO/MnO質量比之關係。第7圖係放大表示第6圖之平均CaO/MnO質量比低之區域。可知將氧含量設為0.0030%以上，就控制氧化物系夾雜物之平均CaO/MnO質量比為低者而言極有效。 Figures 6 and 7 show the relationship between the total oxygen content in the steel materials of each example and the average CaO/MnO mass ratio of oxide-based inclusions. FIG. 7 is an enlarged view showing the area where the average CaO/MnO mass ratio in FIG. 6 is low. It can be seen that setting the oxygen content to 0.0030% or more is extremely effective in controlling the average CaO/MnO mass ratio of oxide-based inclusions to be low.

第8圖中表示有關各例之鋼材中的全部氧含量與熔渣點產生率之關係。可知使用「高純度品」作為脫氧劑之FeSi合金，將氧含量設為0.0030%以上，就抑制熔渣點之產生而言為有效。 Figure 8 shows the relationship between the total oxygen content in the steel materials of each example and the slag point generation rate. It can be seen that the FeSi alloy using the "high purity product" as the deoxidizer has an oxygen content of 0.0030% or more, which is effective in suppressing the generation of slag spots.

第9圖中表示精煉時之熔渣鹼度與熔渣點產生率之關係。可知使用「高純度品」作為脫氧劑之FeSi合金，將熔渣鹼度調整為1.20至1.60之範圍，就抑制熔渣點之產生而言為有效。 Figure 9 shows the relationship between the slag basicity during refining and the slag point generation rate. It can be seen that FeSi alloys using "high-purity products" as deoxidizers are effective in suppressing the occurrence of slag spots by adjusting the slag basicity to a range of 1.20 to 1.60.

Claims (7)

一種不銹鋼材，以質量%計，具有包含C：0.005至0.100%、Si：0.10至3.00%、Mn：0.10至6.50%、P：0.001至0.050%、S：0.0001至0.0200%、Ni：0至20.00%、Cr：10.50至26.00%、Mo：0至2.50%、Cu：0至3.50%、Nb：0至0.500%、V：0至0.500%、Zr：0至0.500%、W：0至0.500%、Co：0至0.500%、B：0至0.020%、N：0.005至0.200%、Ti：0至0.050%、Al：0至0.100%、Ca：0至0.0010%、Mg：0至0.0010%、REM(除了Y以外之稀土元素)：0至0.050%、Y：0至0.050%、O：0.0030至0.0150%、殘部Fe及不可避免的雜質之化學組成，且存在含有Mn之氧化物系夾雜物，在氧化物系夾雜物中之Si、Mn及Ca之含量分別換算成SiO2、MnO及CaO之質量比例時之夾雜物組成中，在金屬組織中所觀察到之氧化物系夾雜物之平均CaO/(SiO2+MnO+CaO)質量比為0.40以下，平均CaO/MnO質量比為15.0以下。 A stainless steel material, in mass %, having C: 0.005 to 0.100%, Si: 0.10 to 3.00%, Mn: 0.10 to 6.50%, P: 0.001 to 0.050%, S: 0.0001 to 0.0200%, Ni: 0 To 20.00%, Cr: 10.50 to 26.00%, Mo: 0 to 2.50%, Cu: 0 to 3.50%, Nb: 0 to 0.500%, V: 0 to 0.500%, Zr: 0 to 0.500%, W: 0 to 0.500%, Co: 0 to 0.500%, B: 0 to 0.020%, N: 0.005 to 0.200%, Ti: 0 to 0.050%, Al: 0 to 0.100%, Ca: 0 to 0.0010%, Mg: 0 to 0.0010 %, REM (rare earth elements other than Y): 0 to 0.050%, Y: 0 to 0.050%, O: 0.0030 to 0.0150%, chemical composition of residual Fe and inevitable impurities, and there are oxide systems containing Mn Inclusions, oxide inclusions observed in the metal structure in the composition of inclusions when the contents of Si, Mn, and Ca in oxide-based inclusions are converted to the mass ratio of SiO 2 , MnO, and CaO, respectively The average CaO/(SiO 2 +MnO+CaO) mass ratio is 0.40 or less, and the average CaO/MnO mass ratio is 15.0 or less. 一種電弧焊接用母材，係包含申請專利範圍第1項所述之不銹鋼材。 A base material for arc welding, including the stainless steel material described in item 1 of the patent application. 一種電弧焊接造管用鋼板母材，係包含申請專利範圍第1項所述之不銹鋼材。 A steel plate base material for arc welding pipe manufacturing, which includes the stainless steel material described in item 1 of the patent application scope. 一種電弧焊接構造構件，係將申請專利範圍第1項所述之不銹鋼材使用於母材中。 An arc welding structural member, which uses the stainless steel material described in item 1 of the patent scope as a base material. 一種電弧焊接鋼管，係將申請專利範圍第1項所述之不 銹鋼材使用於母材中。 An arc-welded steel pipe, which will not be described in item 1 of the patent application Rust steel is used in the base material. 一種焊接構造構件之製造方法，係將申請專利範圍第1項所述之不銹鋼材使用於母材中，且不添加熔填材而進行非消耗性電極式之電弧焊接。 A method for manufacturing a welded structural member, which uses the stainless steel material described in item 1 of the patent scope as a base material, and performs non-consumable electrode arc welding without adding a filler material. 一種焊接鋼管之製造方法，係將申請專利範圍第1項所述之不銹鋼材之鋼板使用於母材中，且不添加熔填材而以非消耗性電極式之電弧焊接形成焊接鋼管。 A method of manufacturing a welded steel pipe, which uses a stainless steel sheet according to item 1 of the patent scope as a base material and forms a welded steel pipe by non-consumable electrode arc welding without adding a filler material.
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