JP2023535587A - Refining slag to obtain CaO-SiO2-MgO low-melting inclusions - Google Patents
Refining slag to obtain CaO-SiO2-MgO low-melting inclusions Download PDFInfo
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- 239000002893 slag Substances 0.000 title claims abstract description 67
- 238000007670 refining Methods 0.000 title claims abstract description 25
- 238000002844 melting Methods 0.000 title claims abstract description 23
- 229910020413 SiO2—MgO Inorganic materials 0.000 title abstract 2
- 238000003723 Smelting Methods 0.000 claims abstract description 36
- 229910000831 Steel Inorganic materials 0.000 claims abstract description 28
- 239000010959 steel Substances 0.000 claims abstract description 28
- 239000000203 mixture Substances 0.000 claims abstract description 14
- 230000008018 melting Effects 0.000 claims abstract description 10
- VYPSYNLAJGMNEJ-UHFFFAOYSA-N Silicium dioxide Chemical compound O=[Si]=O VYPSYNLAJGMNEJ-UHFFFAOYSA-N 0.000 claims abstract description 9
- 229910052681 coesite Inorganic materials 0.000 claims abstract description 5
- 229910052906 cristobalite Inorganic materials 0.000 claims abstract description 5
- 239000000377 silicon dioxide Substances 0.000 claims abstract description 5
- 235000012239 silicon dioxide Nutrition 0.000 claims abstract description 5
- 229910052682 stishovite Inorganic materials 0.000 claims abstract description 5
- 229910052905 tridymite Inorganic materials 0.000 claims abstract description 5
- 229910004298 SiO 2 Inorganic materials 0.000 claims description 19
- 238000000034 method Methods 0.000 claims description 19
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 claims description 18
- 229910052786 argon Inorganic materials 0.000 claims description 9
- 239000007789 gas Substances 0.000 claims description 9
- 229910018072 Al 2 O 3 Inorganic materials 0.000 claims description 6
- 238000010079 rubber tapping Methods 0.000 claims description 5
- 238000010438 heat treatment Methods 0.000 claims description 3
- 238000007664 blowing Methods 0.000 claims description 2
- 230000003628 erosive effect Effects 0.000 abstract description 6
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 abstract description 3
- PNEYBMLMFCGWSK-UHFFFAOYSA-N aluminium oxide Inorganic materials [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 abstract description 2
- 229910052593 corundum Inorganic materials 0.000 abstract description 2
- 238000005516 engineering process Methods 0.000 abstract description 2
- 229910052742 iron Inorganic materials 0.000 abstract description 2
- 239000011819 refractory material Substances 0.000 abstract description 2
- 238000009865 steel metallurgy Methods 0.000 abstract description 2
- 229910001845 yogo sapphire Inorganic materials 0.000 abstract description 2
- 238000005098 hot rolling Methods 0.000 abstract 1
- 238000005096 rolling process Methods 0.000 description 10
- 230000000052 comparative effect Effects 0.000 description 8
- 238000004519 manufacturing process Methods 0.000 description 6
- WUKWITHWXAAZEY-UHFFFAOYSA-L calcium difluoride Chemical compound [F-].[F-].[Ca+2] WUKWITHWXAAZEY-UHFFFAOYSA-L 0.000 description 5
- 229910001634 calcium fluoride Inorganic materials 0.000 description 5
- 238000009749 continuous casting Methods 0.000 description 4
- 230000004907 flux Effects 0.000 description 4
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 3
- 229910052782 aluminium Inorganic materials 0.000 description 3
- -1 aluminum silicon iron Chemical compound 0.000 description 3
- 230000007774 longterm Effects 0.000 description 3
- 229910052748 manganese Inorganic materials 0.000 description 3
- 239000011572 manganese Substances 0.000 description 3
- 229910052751 metal Inorganic materials 0.000 description 3
- 239000002184 metal Substances 0.000 description 3
- 239000010936 titanium Substances 0.000 description 3
- 229910052719 titanium Inorganic materials 0.000 description 3
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 2
- 230000002378 acidificating effect Effects 0.000 description 2
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 2
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 2
- WPBNNNQJVZRUHP-UHFFFAOYSA-L manganese(2+);methyl n-[[2-(methoxycarbonylcarbamothioylamino)phenyl]carbamothioyl]carbamate;n-[2-(sulfidocarbothioylamino)ethyl]carbamodithioate Chemical compound [Mn+2].[S-]C(=S)NCCNC([S-])=S.COC(=O)NC(=S)NC1=CC=CC=C1NC(=S)NC(=O)OC WPBNNNQJVZRUHP-UHFFFAOYSA-L 0.000 description 2
- 239000001301 oxygen Substances 0.000 description 2
- 229910052760 oxygen Inorganic materials 0.000 description 2
- 229910052596 spinel Inorganic materials 0.000 description 2
- 239000011029 spinel Substances 0.000 description 2
- 238000009628 steelmaking Methods 0.000 description 2
- 229910004261 CaF 2 Inorganic materials 0.000 description 1
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 1
- FYYHWMGAXLPEAU-UHFFFAOYSA-N Magnesium Chemical compound [Mg] FYYHWMGAXLPEAU-UHFFFAOYSA-N 0.000 description 1
- MKYBYDHXWVHEJW-UHFFFAOYSA-N N-[1-oxo-1-(2,4,6,7-tetrahydrotriazolo[4,5-c]pyridin-5-yl)propan-2-yl]-2-[[3-(trifluoromethoxy)phenyl]methylamino]pyrimidine-5-carboxamide Chemical compound O=C(C(C)NC(=O)C=1C=NC(=NC=1)NCC1=CC(=CC=C1)OC(F)(F)F)N1CC2=C(CC1)NN=N2 MKYBYDHXWVHEJW-UHFFFAOYSA-N 0.000 description 1
- 229910000639 Spring steel Inorganic materials 0.000 description 1
- 239000002253 acid Substances 0.000 description 1
- 230000002411 adverse Effects 0.000 description 1
- 229910045601 alloy Inorganic materials 0.000 description 1
- 239000000956 alloy Substances 0.000 description 1
- 238000013459 approach Methods 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 229910052799 carbon Inorganic materials 0.000 description 1
- 238000001816 cooling Methods 0.000 description 1
- 238000002425 crystallisation Methods 0.000 description 1
- 230000008025 crystallization Effects 0.000 description 1
- 238000009826 distribution Methods 0.000 description 1
- 229910052749 magnesium Inorganic materials 0.000 description 1
- 239000011777 magnesium Substances 0.000 description 1
- 239000002994 raw material Substances 0.000 description 1
- 229910052710 silicon Inorganic materials 0.000 description 1
- 238000007711 solidification Methods 0.000 description 1
- 230000008023 solidification Effects 0.000 description 1
- 239000002436 steel type Substances 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
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Classifications
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- 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
- C21C5/00—Manufacture of carbon-steel, e.g. plain mild steel, medium carbon steel or cast steel or stainless steel
- C21C5/28—Manufacture of steel in the converter
- C21C5/36—Processes yielding slags of special composition
-
- 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
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
-
- 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
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
-
- 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
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- 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
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
-
- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
- Y02P10/00—Technologies related to metal processing
- Y02P10/20—Recycling
Abstract
本発明によれば、コード鋼の精錬に用いられ、鉄鋼冶金産業の二次精錬技術分野に属する鉄鋼ＣａＯ－ＳｉＯ２－ＭｇＯ系低融点介在物を得る精錬スラグが提供され、その特徴は、合理的に設計される精錬スラグの成分にあり、精錬スラグの各組成の質量百分率は、ＭｇＯ＝１５～２５％、Ａｌ２Ｏ３＜３％であり、残りはＣａＯとＳｉＯ２であり、ＣａＯとＳｉＯ２との質量比は、０．７～１．０である。産業的な適用では、本発明で設計される精錬スラグは低融点ＣａＯ－ＳｉＯ２－ＭｇＯ系介在物を得ることができると示されている。このような介在物は、熱間圧延プロセスにおいて変形が均一で十分であり、最終的に線材中の介在物の幅を２ミクロン以下に制御することができる。同時に、取鍋の耐火材に対する精錬スラグの浸食を低減させ、寿命を２倍以上に向上させることができる。【選択図】図６According to the present invention, there is provided a refined slag used for refining cord steel and obtaining iron and steel CaO-SiO2-MgO-based low-melting inclusions belonging to the secondary refining technology field of the steel metallurgy industry. The mass percentage of each composition of the refined slag is MgO = 15 ~ 25%, Al2O3 <3%, the rest is CaO and SiO2, and the mass ratio of CaO and SiO2 is between 0.7 and 1.0. In industrial applications, it has been shown that the smelting slag designed in the present invention can obtain low melting point CaO--SiO2--MgO inclusions. Such inclusions are uniform and sufficiently deformed in the hot rolling process, and finally the width of the inclusions in the wire can be controlled to 2 microns or less. At the same time, the erosion of the smelting slag on the refractory material of the ladle can be reduced, and the service life can be more than doubled. [Selection drawing] Fig. 6
Description
本発明は、鉄鋼冶金産業の二次精錬技術分野に属し、特にＣａＯ－ＳｉＯ２－ＭｇＯ系低融点介在物を得る精錬スラグに関する。 The present invention belongs to the field of secondary refining technology in the steel metallurgy industry, and particularly relates to refined slag for obtaining CaO-- SiO.sub.2 --MgO-based low-melting inclusions.
コード鋼は、直径０．１５～０．３８ｍｍの鋼線であり、主にタイヤ子午線を作るのに用いられる。コード鋼線は、線径が非常に細く、かつ製造プロセスにおいて力受けが複雑であるため、鋼に寸法が大きく変形しない介在物が存在すると、鋼線は引き抜き又は撚線プロセスにおいて断線することになり、生産効率に悪影響を及ぼし、ひいては製品の格下げや廃棄につながることさえある。研究では、低融点塑性介在物に鋼中の介在物を制御することで、コード鋼の断線率を低下させることができると示されている。 Cord steel is a steel wire with a diameter of 0.15-0.38 mm and is mainly used to make tire meridians. Cord steel wires have a very small wire diameter and are subject to a complicated force-bearing process. This can adversely affect production efficiency and even lead to product downgrades and scrapping. Studies have shown that controlling inclusions in steel to low melting point plastic inclusions can reduce the breakage rate of cord steel.
低融点塑性介在物を得るために、現在、業界では、低アルカリ度酸性ＣａＯ－ＳｉＯ２スラグ系（ＣａＯ／）ＳｉＯ２＝０．８～１．２、Ａｌ２Ｏ３＜１０％、ＭｇＯ＜１０％）を利用して精錬し、スラグ鋼の反応を制御することにより、ＣａＯ－ＳｉＯ２－Ａｌ２Ｏ３－ＭｇＯ低融点領域に介在物を制御する一般的な制御手段が用いられている。現在の精錬工程では、低融点塑性介在物が得られるが、低アルカリ度酸性ＣａＯ－ＳｉＯ２スラグは、取鍋のスラグラインに対する浸食が非常に深刻である。低アルカリ度スラグを用いてコード鋼を製錬する取鍋の寿命は、通常の精錬スラグを用いた寿命の３分の１に過ぎず、さらにより低い。したがって、低アルカリ度酸性スラグによる精錬は、現在、コード鋼の生産プロセスにおいて取鍋の耐火材のコストが高い原因となっている。また、ＣａＯ－ＳｉＯ２－Ａｌ２Ｏ３－ＭｇＯ系低融点介在物は、冷却凝固や長時間に亘る加熱プロセスにおいて二次結晶しやすく、硬質Ａｌ２Ｏ３－ＭｇＯ系スピネル介在物を生成し、このような介在物は変形しない介在物であり、コード鋼の加工プロセスにおける断線を引き起こす可能性が非常に高い。ＣａＯ－ＳｉＯ２－ＭｇＯスラグ系の適用に関するいくつかの手段もある。「ＣＮ２０１６１０５８５０８５．３ばね鋼の精錬方法」などでは、ＣａＯ－ＳｉＯ２－ＭｇＯスラグ系が提案されているが、精錬後の介在物の成分構成や形態が研究されておらず、かつ、この組成の精錬スラグの融点が高く、精錬構成がスラグに溶融しにくいため、ＣａＦ２をフラックスとして別途添加する必要があり、ＣａＦ２の添加は、精錬スラグの融点を低下させる役割を果たすことができるが、ＣａＦ２は、取鍋に対する浸食が非常に深刻であり、同様に取鍋の寿命の低下につながる。また、ＣａＦ２は、環境に優しくないスラグに属し、含まれているＦ元素は、環境を汚染することになり、多くの先進国では、ＣａＦ２は、製鋼スラグにおける使用が明示的に禁止されている。 In order to obtain low melting point plastic inclusions, the industry currently uses low alkalinity acidic CaO-- SiO2 slag-based (CaO/) SiO2 =0.8~1.2, Al2O3 <10%, MgO< 10%) and refining to control the reaction of slag steel, CaO--SiO 2 --Al 2 O 3 --MgO. . The current refining process yields low melting point plastic inclusions, but the low alkalinity acidic CaO--SiO 2 slag is very severely eroding the slag lines of the ladle. The life of ladles smelting cord steel with low alkalinity slag is only one-third of that with normal smelting slag, and even lower. Therefore, smelting with low-alkalinity acid slag is currently responsible for the high cost of ladle refractory materials in the cord steel production process. In addition, CaO-- SiO.sub.2 -- Al.sub.2O.sub.3 -- MgO-based low-melting-point inclusions tend to undergo secondary crystallization during cooling solidification and long-term heating processes, producing hard Al.sub.2O.sub.3 -- MgO -based spinel inclusions. , Such inclusions are non-deformable inclusions, which are very likely to cause wire breakage in the working process of cord steel. There are also some means of applying the CaO--SiO 2 --MgO slag system. In "CN201610585085.3 Refining Method of Spring Steel", etc., a CaO-- SiO.sub.2 --MgO slag system is proposed. Because the melting point of the smelting slag is high, and the smelting structure is difficult to melt into the slag, CaF2 needs to be added separately as a flux. CaF 2 is very severely corrosive to the ladle, also leading to reduced ladle life. In addition, CaF2 belongs to environmentally unfriendly slag, the contained F element will pollute the environment, and in many developed countries, CaF2 is explicitly prohibited from use in steelmaking slag. ing.
したがって、環境にやさしい前提で、ＣａＦ２をフラックスとして含まず、取鍋の寿命を向上させると同時に変形性能が優れている低融点介在物を得る新しいタイプの精錬スラグを如何に設計するかは、本発明が解決すべき技術的問題である。 Therefore, on the premise of being environmentally friendly, how to design a new type of smelting slag that does not contain CaF2 as a flux, improves the life of the ladle and obtains low-melting inclusions with excellent deformation performance. This is a technical problem to be solved by the present invention.
本発明によれば、上記の技術的問題を解決するために、ＣａＯ－ＳｉＯ２－ＭｇＯ系低融点介在物を得る精錬スラグが提供される。 According to the present invention, in order to solve the above technical problems, there is provided a refined slag from which CaO-- SiO.sub.2 --MgO-based low-melting inclusions are obtained.
上記目的を実現するために、本発明で採用される技術的手段は以下のとおりである。 In order to achieve the above object, technical means employed in the present invention are as follows.
ＣａＯ－ＳｉＯ２－ＭｇＯ系低融点介在物を得る精錬スラグにおいて、前記精錬スラグ中の各組成の質量百分率は、ＭｇＯ＝１５～２５％、Ａｌ２Ｏ３＜３％であり、残りはＣａＯとＳｉＯ２であり、ＣａＯとＳｉＯ２との質量比は、０．７～１．０である。 In the refined slag for obtaining CaO-- SiO.sub.2 --MgO-based low-melting inclusions, the mass percentage of each composition in the refined slag is MgO=15-25%, Al.sub.2O.sub.3 <3%, and the rest is CaO. SiO 2 and the mass ratio of CaO to SiO 2 is 0.7 to 1.0.
ＬＦ精錬工程において、電極が加熱されて昇温し、出鋼プロセスにおいて精錬スラグを添加してスラグを作り、ＬＦ処理プロセス全体で取鍋に対してアルゴンガスを底吹きして撹拌し、溶鋼成分が完成品の要求を満たすように溶鋼成分を微調整し、ＬＦ総処理時間≧４５ｍｉｎ、アルゴンガスソフトブロー時間≧２５ｍｉｎである。 In the LF refining process, the electrode is heated to raise the temperature, and in the tapping process, the refining slag is added to make slag, and the entire LF treatment process is stirred by bottom-blowing argon gas into the ladle, and the molten steel composition is Fine-tune the molten steel composition to meet the requirements of the finished product, LF total treatment time ≥ 45min, argon gas soft blow time ≥ 25min.
さらに、ＬＦアルゴンガスソフトブローが完了した後、溶鋼中の酸融解アルミニウムＡｌｓを≦８ｐｐｍに、溶存酸素［Ｏ］を１５～２５ｐｐｍに制御する。 Furthermore, after the LF argon gas soft blow is completed, the acid-melted aluminum Als in the molten steel is controlled to ≦8 ppm and the dissolved oxygen [O] is controlled to 15 to 25 ppm.
好ましくは、ＬＦ総処理時間は、５０ｍｉｎであり、ここで、アルゴンガスソフトブロー時間は、３５ｍｉｎであることが好ましい。 Preferably, the LF total treatment time is 50 min, where the argon gas soft blow time is preferably 35 min.
本発明によれば、アルカリ度（ＣａＯ／ＳｉＯ２）を０．７～１．０範囲にし、ＭｇＯ含有量を１５～２５％に共同して制御し、共同で限定された精錬スラグの１５６５～１５８５℃の精錬温度における精錬時間≧４５ｍｉｎであることが要求されることで、最終的には取鍋の浸食を低下させると同時に変形がより十分な低融点介在物を得ることができ、スラグを溶融して融点を低下させるためにその他のフラックス（ＣａＦ２など）を添加する必要はなく、コストを削減し、環境にやさしいだけではなく、取鍋に対するフラックスの浸食が回避される。 According to the present invention, the alkalinity (CaO/SiO 2 ) is in the range of 0.7-1.0, the MgO content is jointly controlled in the range of 15-25%, and the jointly defined smelting slag It is required that the refining time at the refining temperature of 1585 ° C. is ≧45 min, so that the erosion of the ladle can be reduced and at the same time low-melting inclusions with more sufficient deformation can be obtained, and the slag can be reduced. There is no need to add other fluxes (such as CaF2 ) to melt and lower the melting point, which not only reduces costs and is environmentally friendly, but also avoids flux erosion on the ladle.
本発明の精錬スラグ中のＡｌ２Ｏ３含有量は、２％以内であり、かつ、コード鋼には、一般に低チタン低アルミニウムケイ素鉄と金属マンガン製錬が用いられており、これらの合金のＡｌ含有量が非常に低いため、介在物中のＡｌ２Ｏ３含有量は非常に低く、無視することができ、連続鋳造時に結晶して変形しない硬質ＭｇＯ－Ａｌ２Ｏ３スピネル系介在物を生成することが回避される。本発明で生成されるのは、いずれもコード鋼の断線率を顕著に低下させる十分に変形可能な低融点介在物である。 The Al 2 O 3 content in the smelting slag of the present invention is within 2%, and the cord steel generally uses low titanium low aluminum silicon iron and metal manganese smelting, and these alloys Due to the very low Al content, the Al 2 O 3 content in the inclusions is very low and can be neglected, resulting in hard MgO—Al 2 O 3 spinel inclusions that will not crystallize and deform during continuous casting. avoid generating. All of the inclusions produced by the present invention are sufficiently deformable low-melting inclusions that significantly reduce the breakage rate of cord steel.
従来技術と比較して、本発明の有益な効果は、本発明で提案されるＣａＯ－ＳｉＯ２－ＭｇＯ系低融点介在物を得る精錬スラグを精錬した後にＣａＯ－ＳｉＯ２－ＭｇＯ系低融点介在物を得ると同時にマグネシウム炭素質スラグラインに対する精錬スラグの浸食を効果的に低下させ、従来の工程と比較して、コード鋼の取鍋の寿命を２倍以上に向上させることができ、線材中の酸化物介在物は、圧延方向に沿って変形が十分で均一であり、幅が２ミクロン未満であるため、コード鋼の断線率をさらに低下させる役割が果たされ、コード鋼の取鍋のコストが大幅に低下する。 Compared with the prior art, the beneficial effect of the present invention is that after refining the smelting slag to obtain the CaO—SiO 2 —MgO low melting inclusions proposed in the present invention, the CaO—SiO 2 —MgO low melting inclusions At the same time, it can effectively reduce the erosion of refining slag on the magnesium carbonaceous slag line. The oxide inclusions in the are well and uniformly deformed along the rolling direction and less than 2 microns in width, so they play a role in further reducing the breakage rate of the cord steel, and the ladle of the cord steel significantly lower costs.
以下、図面及び具体的な実施例を参照しながら、本発明についてさらに詳細に説明する。 The present invention will now be described in more detail with reference to the drawings and specific embodiments.
以下の実施例において、試験鋼種はＬＸ８２Ａであり、その化学成分は表１に示され、試験プロセスは、本分野で一般的に用いられるコード鋼の生産工程、すなわち「転炉製鋼」－ＬＦ精錬－連続鋳造－線材圧延」を採用することができ、以下の実施例で採用される試験プロセスは、具体的には以下のとおりである（その他の未公開条件は、いずれもＬＸ８２Ａの通常の製錬条件である）。 In the following examples, the test steel grade is LX82A, its chemical composition is shown in Table 1, the test process is the cord steel production process commonly used in this field, namely "converter steelmaking" - LF refining - Continuous casting - Wire rod rolling" can be adopted, and the test process adopted in the following examples is specifically as follows (other undisclosed conditions are all normal manufacturing conditions of LX82A smelting conditions).
（１）転炉工程において、転炉終点はハイキャッチカーボン工程を採用し、転炉出鋼プロセスにおいて金属マンガン、低チタン低アルミニウムケイ素鉄及び加炭剤を添加する。出鋼が完了した後に金属マンガン、低チタン低アルミニウムケイ素鉄及び本発明で設計される精錬スラグを添加し、金属マンガンと低チタン低アルミニウムケイ素鉄の添加量は、鋼中のＭｎ及びＳｉ含有量が完成品の要求に達し、又は近接することを原則とし、精錬スラグの添加量は、８～１０ｋｇ／トン鋼である。 (1) In the converter process, the end point of the converter adopts the high-catch carbon process, and adds metallic manganese, low-titanium-low-aluminum-silicon-iron and recarburizer in the process of tapping the converter. After tapping is completed, metal manganese, low titanium low aluminum silicon iron and refined slag designed in the present invention are added, and the amount of metal manganese and low titanium low aluminum silicon iron added depends on the Mn and Si content in the steel reaches or approaches the requirements of finished products, and the amount of refined slag added is 8-10 kg/ton steel.
（２）ＬＦ精錬工程において、電極が加熱されて昇温し、加熱温度を１５６５～１５８５℃（好ましくは１５７０℃）に制御し、出鋼プロセスにおいて添加された精錬スラグ（１＃－７＃のいずれか）に対してスラグを作り、ＬＦ処理プロセス全体で取鍋に対してアルゴンガスを底吹きして撹拌し、溶鋼成分が完成品の要求を満たすように溶鋼成分を微調整し、ＬＦ総処理時間≧４５ｍｉｎ（好ましくは５０ｍｉｎ）、アルゴンガスソフトブロー時間≧２５ｍｉｎ（好ましくは３５ｍｉｎ）である。ＬＦアルゴンガスソフトブローが完了した後、溶鋼中の酸融解アルミニウムＡｌｓを≦８ｐｐｍに、溶存酸素［Ｏ］を１５～２５ｐｐｍに制御する。 (2) In the LF refining process, the electrode is heated to raise the temperature, the heating temperature is controlled to 1565 to 1585 ° C. (preferably 1570 ° C.), and the refined slag (1#-7#) added in the tapping process Either) is made into slag, argon gas is bottom-blown into the ladle and stirred throughout the LF treatment process, the molten steel composition is fine-tuned so that it meets the requirements of the finished product, and the LF total Treatment time≧45 min (preferably 50 min), argon gas soft blow time≧25 min (preferably 35 min). After the LF argon gas soft blow is completed, the acid-melted aluminum Als in the molten steel is controlled to ≦8 ppm and the dissolved oxygen [O] is controlled to 15-25 ppm.
（３）連続鋳造及び線材圧延工程において、連続鋳造により１６０ｍｍ×１６０ｍｍの小ビレットが得られ、小ビレットを１０５０－１１００℃に加熱し、２時間保温し、直径５．５ｍｍのコード鋼線材に圧延する。
（実施例１）
(3) In the continuous casting and wire rod rolling process, a small billet of 160 mm × 160 mm is obtained by continuous casting, the small billet is heated to 1050-1100 ° C., held for 2 hours, and rolled into a cord steel wire rod with a diameter of 5.5 mm. do.
(Example 1)
本実施例で取鍋に添加した精錬スラグは、表２に示す１＃精錬スラグである。
（実施例２）
The smelting slag added to the ladle in this example is the 1# smelting slag shown in Table 2.
(Example 2)
本実施例で取鍋に添加した精錬スラグは、表２に示す２＃精錬スラグである。
（実施例３）
The smelting slag added to the ladle in this example is the 2# smelting slag shown in Table 2.
(Example 3)
本実施例で取鍋に添加した精錬スラグは、表２に示す３＃精錬スラグである。
（実施例４）
The smelting slag added to the ladle in this example is the 3# smelting slag shown in Table 2.
(Example 4)
本実施例で取鍋に添加した精錬スラグは、表２に示す４＃精錬スラグである。
（比較例１）
The smelting slag added to the ladle in this example is the 4# smelting slag shown in Table 2.
(Comparative example 1)
本実施例で取鍋に添加した精錬スラグは、表３に示す５＃精錬スラグである。 The smelting slag added to the ladle in this example is the 5# smelting slag shown in Table 3.
精錬スラグのアルカリ度は、１．０よりも高く、図７から分かるように、生産用線材中の介在物にはマグネシウムアルミニウムスピネルが析出し、介在物は、変形が不十分であり、塊状をなし、断線のリスクが高まる。
（比較例２）
The alkalinity of the smelting slag is higher than 1.0, and as can be seen from FIG. None, increased risk of disconnection.
(Comparative example 2)
本実施例で取鍋に添加した精錬スラグは、表３に示す６＃精錬スラグである。 The smelting slag added to the ladle in this example is the 6# smelting slag shown in Table 3.
介在物中のＡｌ２Ｏ３含有量は、３％よりも高く、図８から分かるように、線材中の介在物にはマグネシウムアルミニウムスピネルが析出し、介在物は、変形が不十分であり、塊状をなし、断線のリスクが高まる。
（比較例３）
The Al 2 O 3 content in the inclusions is higher than 3%, and as can be seen from FIG. It forms lumps and increases the risk of disconnection.
(Comparative Example 3)
本実施例で取鍋に添加した精錬スラグは、表３に示す７＃精錬スラグであり、取鍋の寿命が終了するまで製錬し、取鍋の寿命を統計する。 The smelting slag added to the ladle in this example is the 7# smelting slag shown in Table 3, which is smelted until the end of the life of the ladle and statistics of the life of the ladle.
ＭｇＯ含有量は、１５％未満であり、耐火材中のＭｇＯが精錬スラグに多量に溶解することになり、耐火材の浸食が非常に深刻であり、寿命が低下する。 The MgO content is less than 15%, which will cause a large amount of MgO in the refractory to dissolve into the refining slag, and the erosion of the refractory will be very serious, reducing the service life.
上記実施例で得られた線材をそれぞれ取り、走査型電子顕微鏡を用いて酸化物介在物の圧延方向に沿った形態を検査する。図１～図４は、それぞれ実施例１～４で得られた線材中の酸化物介在物の圧延方向に沿った形態であり、本発明の精錬スラグを用いて得られた線材中の酸化物は、圧延方向に沿って変形が十分で均一であり、横方向の幅が２ミクロン以下であり、ほとんどの介在物の寸法幅は、図５に示すように１．２ミクロン以下である。 Each of the wires obtained in the above examples is taken and inspected for oxide inclusions along the rolling direction using a scanning electron microscope. 1 to 4 show the shapes along the rolling direction of oxide inclusions in the wire rods obtained in Examples 1 to 4, respectively. has a good and uniform deformation along the rolling direction, a lateral width of 2 microns or less, and most inclusions have a dimension width of 1.2 microns or less as shown in FIG.
図６は、実施例１－４に係る介在物の成分の投影であり、介在物の成分は、ＣａＯ－ＳｉＯ２－ＭｇＯであり、ＣａＯ－ＳｉＯ２－ＭｇＯ系低融点領域にある。 FIG. 6 is a projection of the composition of the inclusions according to Example 1-4. The composition of the inclusions is CaO-- SiO.sub.2 --MgO, which is in the CaO-- SiO.sub.2 --MgO system low melting point region.
図７及び図８は、それぞれ比較例１及び比較例２で得られた介在物の成分及び形態であり、介在物にはマグネシウムアルミニウムスピネルが析出し、介在物は、変形が不十分であり、塊状をなす。 7 and 8 show the composition and morphology of the inclusions obtained in Comparative Examples 1 and 2, respectively. form lumps.
また、長期に亘る生産実践では、比較例３に用いられる精錬スラグ（現在コード鋼の通常の精錬スラグを代表する）を採用する取鍋の寿命範囲は２３～２９炉（平均２５炉）でまちまちであり、本発明の精錬スラグを採用して長期に生産した後に寿命を７１～８３炉（平均７６炉）に向上させることができると示されている。 Also, in long-term production practice, the life range of ladles employing the smelting slag used in Comparative Example 3 (representing the usual smelting slag for cord steel today) varies from 23 to 29 furnaces (25 furnaces on average). , and it is shown that the life can be improved to 71-83 furnaces (76 furnaces on average) after long-term production using the smelting slag of the present invention.
表１ 試験鋼種ＬＸ８２Ａの成分、質量百分率
上記実施例における１＃、２＃、３＃、４＃精錬スラグは、それぞれ表２に示す原料の比率に従って調製され、均一に混合される。 The 1#, 2#, 3#, and 4# smelting slags in the above examples were each prepared according to the raw material ratios shown in Table 2 and uniformly mixed.
表２ 実施例に用いられる精錬スラグの成分、質量百分率
表３ 比較例に用いられる精錬スラグの成分、質量百分率
最後に、上記の具体的な実施形態は、本発明の技術的手段を説明するためのものに過ぎず、それを制限するものではないことを説明すべきである。実施例を参照しながら本発明について詳細に説明したが当業者は、本発明の技術的手段の精神と範囲から逸脱することなく、本発明の技術的手段を修正又は同等に置換することができることを理解する必要があり、それらは、いずれも本発明の特許請求の範囲に含まれるべきである。 Finally, it should be explained that the above specific embodiments are only for explaining the technical means of the present invention and not for limiting it. Although the present invention has been described in detail with reference to the embodiments, those skilled in the art can modify or equivalently replace the technical means of the present invention without departing from the spirit and scope of the technical means of the present invention. should be understood and should all be included in the claims of the present invention.
Claims (4)
前記精錬スラグ中の各組成の質量百分率は、ＭｇＯ＝１５～２５％、Ａｌ２Ｏ３＜３％であり、残りがＣａＯとＳｉＯ２である、
ことを特徴とするＣａＯ－ＳｉＯ２－ＭｇＯ系低融点介在物を得る精錬スラグ。 Refining slag for obtaining CaO—SiO 2 —MgO-based low-melting inclusions,
The mass percentage of each composition in the smelting slag is MgO=15-25%, Al 2 O 3 <3%, and the balance is CaO and SiO 2 .
Refining slag for obtaining CaO--SiO 2 --MgO-based low-melting inclusions characterized by:
ことを特徴とする請求項１に記載のＣａＯ－ＳｉＯ２－ＭｇＯ系低融点介在物を得る精錬スラグ。 The mass ratio of CaO and SiO2 in the smelting slag is 0.7 to 1.0.
Refining slag for obtaining CaO--SiO 2 --MgO-based low-melting inclusions according to claim 1, characterized in that:
ＬＦ精錬工程において、電極が加熱されて昇温し、出鋼プロセスにおいて精錬スラグを添加してスラグを作り、ＬＦ処理プロセス全体で取鍋に対してアルゴンガスを底吹きして撹拌し、溶鋼成分が完成品の要求を満たすように溶鋼成分を微調整し、ＬＦ総処理時間≧４５ｍｉｎ、アルゴンガスソフトブロー時間≧２５ｍｉｎでＣａＯ－ＳｉＯ２－ＭｇＯ系低融点介在物を得ることである、
ことを特徴とする請求項１又は２に記載のＣａＯ－ＳｉＯ２－ＭｇＯ系低融点介在物を得る精錬スラグ。 The application of refining slag in the LF refining process is
In the LF refining process, the electrode is heated to raise the temperature, and in the tapping process, the refining slag is added to make slag, and the entire LF treatment process is stirred by bottom-blowing argon gas into the ladle, and the molten steel composition is is to fine-tune the molten steel composition to meet the requirements of the finished product, and obtain CaO-SiO 2 -MgO system low melting point inclusions with LF total treatment time ≥ 45min and argon gas soft blow time ≥ 25min.
Refining slag for obtaining CaO--SiO 2 --MgO-based low-melting inclusions according to claim 1 or 2, characterized in that:
ことを特徴とする請求項３に記載のＣａＯ－ＳｉＯ２－ＭｇＯ系低融点介在物を得る精錬スラグ。 The heating temperature of the LF electrode is controlled from 1565 to 1585 ° C.
Refining slag for obtaining CaO--SiO 2 --MgO-based low-melting inclusions according to claim 3, characterized in that:
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