JP2007262460A - Hot rolled wire rod - Google Patents
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- JP2007262460A JP2007262460A JP2006087126A JP2006087126A JP2007262460A JP 2007262460 A JP2007262460 A JP 2007262460A JP 2006087126 A JP2006087126 A JP 2006087126A JP 2006087126 A JP2006087126 A JP 2006087126A JP 2007262460 A JP2007262460 A JP 2007262460A
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- 229910001039 duplex stainless steel Inorganic materials 0.000 claims abstract description 24
- 229910000859 α-Fe Inorganic materials 0.000 claims abstract description 16
- 229910052802 copper Inorganic materials 0.000 claims abstract description 5
- 229910052758 niobium Inorganic materials 0.000 claims abstract description 5
- 229910052719 titanium Inorganic materials 0.000 claims abstract description 5
- 229910052721 tungsten Inorganic materials 0.000 claims abstract description 5
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 3
- 229910052759 nickel Inorganic materials 0.000 claims abstract description 3
- 229910052757 nitrogen Inorganic materials 0.000 claims abstract description 3
- 229910052804 chromium Inorganic materials 0.000 claims abstract 2
- 238000005098 hot rolling Methods 0.000 abstract description 13
- 238000005491 wire drawing Methods 0.000 abstract description 8
- 229910001566 austenite Inorganic materials 0.000 abstract description 2
- 229910052799 carbon Inorganic materials 0.000 abstract description 2
- 229910052750 molybdenum Inorganic materials 0.000 abstract description 2
- 238000005096 rolling process Methods 0.000 description 51
- 238000000034 method Methods 0.000 description 9
- 239000000126 substance Substances 0.000 description 9
- 239000000203 mixture Substances 0.000 description 8
- 230000007797 corrosion Effects 0.000 description 7
- 238000005260 corrosion Methods 0.000 description 7
- 230000000694 effects Effects 0.000 description 7
- 229910000831 Steel Inorganic materials 0.000 description 5
- 230000000052 comparative effect Effects 0.000 description 5
- 230000007547 defect Effects 0.000 description 5
- 239000010959 steel Substances 0.000 description 5
- 238000010438 heat treatment Methods 0.000 description 4
- MUBZPKHOEPUJKR-UHFFFAOYSA-N Oxalic acid Chemical compound OC(=O)C(O)=O MUBZPKHOEPUJKR-UHFFFAOYSA-N 0.000 description 3
- 230000001276 controlling effect Effects 0.000 description 3
- 239000000463 material Substances 0.000 description 3
- 238000005482 strain hardening Methods 0.000 description 3
- 238000000137 annealing Methods 0.000 description 2
- 238000005336 cracking Methods 0.000 description 2
- 238000011156 evaluation Methods 0.000 description 2
- 238000005554 pickling Methods 0.000 description 2
- 206010070834 Sensitisation Diseases 0.000 description 1
- 238000007792 addition Methods 0.000 description 1
- 230000006399 behavior Effects 0.000 description 1
- 239000003153 chemical reaction reagent Substances 0.000 description 1
- 238000005097 cold rolling Methods 0.000 description 1
- 238000004040 coloring Methods 0.000 description 1
- 238000001816 cooling Methods 0.000 description 1
- 238000000866 electrolytic etching Methods 0.000 description 1
- 238000010191 image analysis Methods 0.000 description 1
- 239000012535 impurity Substances 0.000 description 1
- 230000006698 induction Effects 0.000 description 1
- 238000011835 investigation Methods 0.000 description 1
- 238000004519 manufacturing process Methods 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 235000006408 oxalic acid Nutrition 0.000 description 1
- 229910052760 oxygen Inorganic materials 0.000 description 1
- 230000035515 penetration Effects 0.000 description 1
- 229910052698 phosphorus Inorganic materials 0.000 description 1
- 238000005498 polishing Methods 0.000 description 1
- 238000001953 recrystallisation Methods 0.000 description 1
- 230000001105 regulatory effect Effects 0.000 description 1
- 230000008313 sensitization Effects 0.000 description 1
- 238000002791 soaking Methods 0.000 description 1
- 229910052717 sulfur Inorganic materials 0.000 description 1
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 1
- 238000003466 welding Methods 0.000 description 1
- 230000037303 wrinkles Effects 0.000 description 1
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- Heat Treatment Of Steel (AREA)
Abstract
Description
本発明は、フェライト・オーステナイト２相ステンレス鋼線材に係わり、圧延の総歪み量，仕上げ圧延速度や仕上げ圧延温度を正確に制御することで表面疵の発生を抑制して低コスト且つ安定的に大単重の細径線材を提供するものである。 The present invention relates to a ferrite-austenitic duplex stainless steel wire rod, and by controlling the total amount of rolling distortion, finishing rolling speed, and finishing rolling temperature accurately, the occurrence of surface flaws can be suppressed and stably produced at low cost. The present invention provides a single thin wire rod.
２相ステンレス鋼は、優れた耐食性と機械的性質を有するため化学プラント等の機械構造物やその溶接棒等に使われてきた。しかしながら、熱間圧延中のオーステナイト相とフェライト相の２相組織の変形挙動差およびその界面剥離性に起因して熱間圧延時の表面疵が問題になることが多かった。
これまで、２相ステンレス鋼の熱間圧延での製造方法に関して、Ｓ量を規制し、鋳片でソーキング処理を施して熱間加工性を向上させることが提案されている（特許文献１）。
また、２相ステンレス鋼はσ相が生成し易く、熱間圧延中にσ相が生成すると表面疵が発生するため、σ相の生成を防止する熱間圧延方法が提案されている（特許文献２）。
さらに、２相ステンレス鋼の熱間での超塑性変形方法も提案されている（特許文献３）。
Since duplex stainless steel has excellent corrosion resistance and mechanical properties, it has been used for mechanical structures such as chemical plants and welding rods thereof. However, due to the difference in deformation behavior of the two-phase structure of the austenite phase and ferrite phase during hot rolling and the interfacial peelability, surface defects during hot rolling often become a problem.
Until now, regarding the manufacturing method by hot rolling of duplex stainless steel, it has been proposed to improve the hot workability by regulating the amount of S and performing a soaking process with a slab (Patent Document 1).
In addition, a duplex stainless steel easily generates a σ phase, and when the σ phase is generated during hot rolling, surface flaws are generated, so a hot rolling method for preventing the generation of the σ phase has been proposed (Patent Document). 2).
Furthermore, a hot superplastic deformation method of duplex stainless steel has also been proposed (Patent Document 3).
一方、２相ステンレス鋼線材の一般的な連続線材圧延において、一回でφ８ｍｍ以下の細径に熱間圧延すると仕上げ圧延にて表面疵が多発していた。そのため、一度、φ８ｍｍ超の線径に熱間線材圧延を施した後に、再加熱して特殊なミニミルにて細径線材へ熱間圧延していた。しかしながら、この場合、加熱炉制約により通常の線材に求められる大単重化（≧４００ｋｇ）が困難となっていた。また、特殊なミニミルで再熱間圧延ができない場合は、φ８ｍｍ超の線径に熱間線材圧延を施した後に冷間伸線加工（冷間圧延含む）と焼鈍を繰り返して細径鋼線にしていた。そのため、いずれにしても、これまで２相ステンレス鋼線材は、納期，コスト，大単重の点で劣っており、その後の冷間伸線加工時に経済性を発揮させることができず、細軽２相ステンレス鋼線の普及の障害となっていた。 On the other hand, in general continuous wire rolling of a duplex stainless steel wire rod, hot rolling to a small diameter of φ8 mm or less at one time resulted in frequent surface flaws in finish rolling. Therefore, after hot wire rolling was performed once on a wire diameter exceeding φ8 mm, it was reheated and hot-rolled to a thin wire with a special mini mill. However, in this case, it has been difficult to achieve a large unit weight (≧ 400 kg) required for ordinary wire rods due to heating furnace restrictions. If re-hot rolling is not possible with a special mini mill, hot wire rolling is applied to a wire diameter exceeding φ8 mm, and then cold wire drawing (including cold rolling) and annealing are repeated to obtain a thin steel wire. It was. Therefore, in any case, the duplex stainless steel wire has been inferior in terms of delivery time, cost, and large unit weight, and cannot be economically demonstrated during the subsequent cold wire drawing, and is light. It was an obstacle to the spread of duplex stainless steel wires.
以上、２相ステンレス鋼の細径線材において、従来の提案技術では表面疵が発生するばかりか、表面疵を回避する手法をとれば、経済性に劣る４００ｋｇ未満の小単重の線材コイルしか存在しなかった。
本発明の目的は、細径の２相ステンレス鋼線材の熱間線材圧延条件を正確に制御することにより、表面疵の発生を防止し、低コストで安定して大単重の細径線材を提供することにある。 The object of the present invention is to accurately control the hot wire rolling conditions of a small-diameter duplex stainless steel wire rod, thereby preventing the occurrence of surface flaws and stably producing a large single-weight thin wire rod at low cost. It is to provide.
本発明者らは、上記課題を解決するために種々検討した結果、連続線材圧延での総歪み量，仕上げ圧延速度および圧延温度を正確に制御することで、安定且つ低コストに大単重の細径線材を提供できることを見出した。本発明は、上記知見に基づいてなされたものであり、その要旨とするところは以下の通りである。
すなわち、本発明の要旨とするところは以下の通りである。
（１）質量％で、Ｃ；０．００５〜０．１５％，Ｓｉ；０．１〜３．５％，Ｍｎ；０．１〜１０．０％，Ｎｉ；１．０〜１５．０％，Ｃｒ；１３．０〜４０．０％，Ｎ；０．００５〜０．４０％を含有し、フェライト相の面積率が２５〜８０％であるオーステナイト・フェライト２相ステンレス鋼線材で、線径が４．５〜８ｍｍ，コイル単重が４００kg以上であることを特徴とする熱間圧延線材である。
（２）質量％で、Ｍｏ；６．０％以下，Ｃｕ；４．０％以下，Ｗ；１．０％以下，Ｎｂ；１．０％以下，Ｔｉ；１．０％以下の１種以上を含有することを特徴とする前記（１）に記載の熱間圧延線材である。
As a result of various investigations to solve the above problems, the present inventors have accurately controlled the total strain amount, finish rolling speed, and rolling temperature in continuous wire rod rolling, so that a large unit weight can be obtained stably and at low cost. It has been found that a thin wire can be provided. This invention is made | formed based on the said knowledge, The place made into the summary is as follows.
That is, the gist of the present invention is as follows.
(1) By mass%, C; 0.005 to 0.15%, Si; 0.1 to 3.5%, Mn; 0.1 to 10.0%, Ni; 1.0 to 15.0% , Cr; 13.0 to 40.0%, N; 0.005 to 0.40%, and a ferrite phase area ratio of 25 to 80%. 4.5 to 8 mm, and the coil single weight is 400 kg or more.
(2) 1% or more of Mo; 6.0% or less, Cu; 4.0% or less, W; 1.0% or less, Nb; 1.0% or less, Ti; The hot-rolled wire rod according to (1) above, which contains
本発明による２相ステンレス鋼線材は、冷間伸線加工の素材として大単重の細径熱
間線材を安定且つ低コストに提供できるため、２相ステンレス鋼線の市場への普及率を飛躍的に高める効果を発揮する。
Since the duplex stainless steel wire according to the present invention can provide a large single-piece thin-diameter hot wire as a material for cold wire drawing stably and at low cost, the penetration rate of the duplex stainless steel wire to the market has jumped. To enhance the effect.
以下に、本発明の請求項１に記載の限定理由について説明する。
化学組成は、鋼中のフェライト相の面積率が２５％〜８０％を得るために決められたものであり、通常の２相ステンレス鋼の化学組成であるが、とりわけ、成分限定理由について記述する。
The reason for limitation described in claim 1 of the present invention will be described below.
The chemical composition is determined in order to obtain an area ratio of the ferrite phase in the steel of 25% to 80%, and is a chemical composition of a normal duplex stainless steel. .
以下に示す化学組成は全て質量％を示す。
Ｃは、２相ステンレス鋼線材の強度を付与するために０．００５％以上添加されるが、０．１５％を超えると鋭敏化により耐食性が劣化する。そのため、０．００５〜０．１５％に限定する。
Ｓｉは、脱酸に必要な元素であり、０．１％以上添加されるが、３．５％を超えると延性がなくなり、材質劣化する。そのため、０．１〜３．５％に限定する。
Ｍｎは、脱酸に必要な元素であり、０．１％以上添加されるが、１０％を超えると耐食性が劣化する。そのため、０．１〜１０．０％に限定する。
The chemical compositions shown below all represent mass%.
C is added in an amount of 0.005% or more in order to give the strength of the duplex stainless steel wire, but if it exceeds 0.15%, the corrosion resistance deteriorates due to sensitization. Therefore, it is limited to 0.005 to 0.15%.
Si is an element necessary for deoxidation and is added in an amount of 0.1% or more. However, if it exceeds 3.5%, the ductility is lost and the material deteriorates. Therefore, it is limited to 0.1 to 3.5%.
Mn is an element necessary for deoxidation, and is added in an amount of 0.1% or more. However, if it exceeds 10%, the corrosion resistance deteriorates. Therefore, it is limited to 0.1 to 10.0%.
Ｎｉは、２相組織を得て耐食性を確保するために１．０％以上添加されるが、１５％を超えて添加されると２相組織が得られなくなる。そのため、１．０〜１５．０％に限定する。
Ｃｒは、耐食性を確保するために１３．０％以上添加されるが、４０．０％を超えて添加されると延性が劣化し、材質劣化する。そのため、１３．０〜４０．０％に限定する。
Ｎは、２相ステンレス鋼線材の強度を付与するために０．００５％以上添加されるが、０．４％を超えて添加されると気泡の発生により製造性が劣化する。そのため、０．００５〜０．４０％に限定する。
Ni is added in an amount of 1.0% or more in order to obtain a two-phase structure and ensure corrosion resistance. However, if it exceeds 15%, a two-phase structure cannot be obtained. Therefore, it is limited to 1.0 to 15.0%.
Cr is added in an amount of 13.0% or more in order to ensure corrosion resistance. However, if it exceeds 40.0%, the ductility deteriorates and the material deteriorates. Therefore, it is limited to 13.0-40.0%.
N is added in an amount of 0.005% or more in order to give the strength of the duplex stainless steel wire, but if added over 0.4%, the productivity deteriorates due to the generation of bubbles. Therefore, it is limited to 0.005 to 0.40%.
次にフェライト相の面積率の限定理由について述べる。
フェライト相の面積率が２５％未満の場合、熱間加工性が低下するため熱間圧延疵が多発するため、本発明の効果がなくなる。一方、フェライト相の面積率が８０％を超えると線材圧延中の再結晶が促進されるため、通常の線材圧延工程で加工剪断割れが発生し難くなり、本発明の効果がなくなる。従って、本発明の効果が最大限に発揮できるように、フェライト相の面積率を２５〜８０％に限定する。好ましくは、３０〜７５％である。
Next, the reason for limiting the area ratio of the ferrite phase will be described.
When the area ratio of the ferrite phase is less than 25%, the hot workability is deteriorated and hot rolling defects occur frequently, so the effect of the present invention is lost. On the other hand, if the area ratio of the ferrite phase exceeds 80%, recrystallization during wire rolling is promoted, so that it becomes difficult for processing shear cracks to occur in a normal wire rolling process, and the effect of the present invention is lost. Therefore, the area ratio of the ferrite phase is limited to 25 to 80% so that the effects of the present invention can be maximized. Preferably, it is 30 to 75%.
次に線材製品の線径の限定理由について述べる。２相ステンレス鋼は熱間で再結晶し難い特徴を有するため、熱間線材圧延のように約２〜５分程度の短時間に大きな加工歪み（圧延減面率で９９％以上）を導入する場合、その途中工程で再結晶し難いために加工硬化して最終の仕上げ圧延工程で加工剪断割れを起こす。そのため、連続線材圧延で導入する総歪み量，仕上げ圧延速度，仕上げ圧延温度を正確に制御する必要がある。すなわち、連続線材圧延での総歪み量を小さく，仕上げ圧延速度を遅く，仕上げ圧延温度を高くしなければ仕上げ圧延にて加工硬化して加工剪断割れが発生する。
ここで線径が８ｍｍを超えた場合、通常の連続線材圧延での総歪み量が小さく、仕上げ圧延での加工硬化が小さくなるため、無疵にて線材圧延が可能となるが、その後の冷間伸線加工の伸線減面率が大きくなり、経済性に劣る。一方、線径が４．５ｍｍ未満になると熱間での加工硬化が大きくなり、加工剪断割れが発生し易くなり、経済性を発揮できなくなる。そのため、線材製品の線径を本発明の効果が発揮できる４．５〜８．０ｍｍに限定する。好ましくは、５．０〜７．５ｍｍである。
Next, the reason for limiting the wire diameter of the wire product will be described. Since duplex stainless steel has the feature that it is difficult to recrystallize hot, a large working strain (99% or more rolling reduction) is introduced in a short time of about 2 to 5 minutes as in hot wire rolling. In this case, since it is difficult to recrystallize in the middle of the process, it is work-hardened and causes a work shear crack in the final finish rolling process. Therefore, it is necessary to accurately control the total strain amount, finish rolling speed, and finish rolling temperature introduced in continuous wire rolling. That is, if the total strain in continuous wire rolling is small, the finish rolling speed is slow, and the finish rolling temperature is not high, work hardening occurs in finish rolling and work shear cracks occur.
Here, when the wire diameter exceeds 8 mm, the total strain amount in the normal continuous wire rolling is small, and the work hardening in the finish rolling is small. The wire drawing area reduction rate of the wire drawing process is large, and the economy is inferior. On the other hand, when the wire diameter is less than 4.5 mm, work hardening in the hot state is increased, work shear cracks are likely to occur, and economic efficiency cannot be exhibited. Therefore, the wire diameter of the wire product is limited to 4.5 to 8.0 mm at which the effect of the present invention can be exhibited. Preferably, it is 5.0-7.5 mm.
線材のコイル単重は、４００ｋｇ未満の場合、特殊なミニミルを用いれば、熱間圧延での総歪み量が小さいためにφ８ｍｍ以下へ容易に熱間圧延が可能となるが、加熱炉制約のために４００ｋｇ以上の大単重化が図れず、その後の冷間伸線加工工程で経済性を発揮できない。そのため、通常の大単重の連続線材圧延で本発明の効果が得られるようコイル単重を４００ｋｇ以上に限定する。好ましくは、７００ｋｇ以上である。
なお、本発明での連続線材圧延とは、各圧延スタンド間の圧延待ち時間が３０秒を超えない１５段以上の多段スタンドを有する連続圧延工程を言う。
また、熱間圧延線材とは、熱間圧延後に水冷、または熱間圧延直後にインライン熱処理が施されて水冷された線材コイルを示し、また必要に応じて酸洗された線材コイルのことを言う。
When the coil weight of the wire is less than 400 kg, if a special mini mill is used, the total amount of strain in hot rolling is small, so that hot rolling can be easily performed to φ8 mm or less, but due to restrictions in the heating furnace In addition, a large unit weight of 400 kg or more cannot be achieved, and economical efficiency cannot be exhibited in the subsequent cold wire drawing process. For this reason, the coil unit weight is limited to 400 kg or more so that the effect of the present invention can be obtained by ordinary large unit weight continuous wire rod rolling. Preferably, it is 700 kg or more.
The continuous wire rolling in the present invention refers to a continuous rolling process having 15 or more multi-stage stands in which the rolling waiting time between the rolling stands does not exceed 30 seconds.
The hot-rolled wire rod refers to a wire coil that is water-cooled after hot rolling or subjected to in-line heat treatment immediately after hot rolling and water-cooled, and is pickled as necessary. .
次に、請求項２に記載の限定理由について述べる。
化学組成は、鋼中のフェライト相の面積率が２５％〜８０％を得るために決められたものであり、通常の２相ステンレス鋼の化学組成であるが、とりわけ、更に耐食性を向上させる成分限定理由について記述する。
Ｍｏ，Ｃｕ，Ｗ，Ｎｂ，Ｔｉは、２相ステンレス鋼線材の耐食性を向上させる有効な元素であり、必要に応じて添加されるが、過剰に添加すると経済性に劣る。そのため、Ｍｏ；６．０％以下，Ｃｕ；４．０％以下，Ｗ；１．０％以下，Ｎｂ；１．０％以下，Ｔｉ；１．０％以下の１種類以上の添加に限定する。
Next, the reason for limitation described in claim 2 will be described.
The chemical composition is determined in order to obtain an area ratio of the ferrite phase in the steel of 25% to 80%, and is a chemical composition of a normal duplex stainless steel. In particular, the component further improves the corrosion resistance. Describe the reason for the limitation.
Mo, Cu, W, Nb, and Ti are effective elements that improve the corrosion resistance of the duplex stainless steel wire, and are added as necessary. However, if added excessively, the economy is inferior. Therefore, it is limited to one or more additions of Mo; 6.0% or less, Cu; 4.0% or less, W; 1.0% or less, Nb; 1.0% or less, Ti; .
ここで、本発明対象の２相ステンレス鋼の化学組成は、前述した以外に、必要に応じて、Ａｌ；０．００２〜０．１％，Ｓ；０．０１％以下，Ｐ；０．０５％以下，Ｃａ；０．０１％以下，Ｍｇ；０．０１％以下，Ｏ；０．０１５％以下の１種類以上を含有し、残部はＦｅおよび不可避的不純物からなる。 Here, in addition to the chemical composition of the duplex stainless steel of the present invention, Al; 0.002 to 0.1%, S; 0.01% or less, P; 0.05, if necessary. %, Ca; 0.01% or less, Mg; 0.01% or less, O; 0.015% or less. The balance is Fe and inevitable impurities.
以下に本発明の実施例について説明する。
表１に実施例の鋼の化学組成を示す。
Table 1 shows the chemical composition of the steels of the examples.
これら化学組成の鋼は、２ｔの真空溶解炉にて溶解し、熱間鍛造を施してφ７０〜２００ｍｍで長さ８ｍｍの線材圧延用のビレットに仕上げた（単重を０．２〜２ｔに変化させた）。その後、様々な条件にてφ７．５〜５．０ｍｍまで熱間線材圧延を行った。一部については、連続線材圧延中に高周波誘導加熱を付与して圧延温度を意図的に上昇させた。連続線材圧延後は直ちに水冷を行い、その後、酸洗を施し、線材表面疵の有無を判定した。 Steels with these chemical compositions were melted in a 2t vacuum melting furnace, hot forged, and finished into billets for rolling wire rods with a diameter of 70 to 200mm and a length of 8mm (single weight changed to 0.2 to 2t) ) Thereafter, hot wire rolling was performed to φ7.5 to 5.0 mm under various conditions. For some, high-frequency induction heating was applied during continuous wire rod rolling to intentionally raise the rolling temperature. Immediately after the continuous wire rolling, water cooling was performed, and then pickling was performed to determine the presence or absence of wire surface defects.
線材表面疵の評価は、酸洗後の線材コイルを１リングづつ目視にて判定した。また、フェライト相の面積率は線材を縦断面に埋め込み研磨し、蓚酸電解エッチ後に村上試薬にてフェライト相に着色し、画像解析にて判定した。圧延条件および評価結果を表２に示す。 The evaluation of the surface defects on the wire was made by visually observing the wire coil after pickling one ring at a time. The area ratio of the ferrite phase was determined by image analysis by embedding and polishing a wire in a longitudinal section, coloring the ferrite phase with Murakami reagent after oxalic acid electrolytic etching. Table 2 shows rolling conditions and evaluation results.
本発明例では、フェライト相の面積率を２５〜８０％の範囲内にし、連続線材圧延の総歪み量（＝ｌｎ（圧延前の断面積／圧延後の断面積））を６．５以下，且つ、仕上げ圧延速度を８５ｍ／ｓ以下，且つ、仕上げ圧延温度を１０００℃以上に正確に制御（条件(a)）することで表面疵が発生することなくビレットからの１回の熱間線材圧延によりφ８ｍｍ以下の細径，４００ｋｇ以上の大単重コイルに製造ができている。 In the present invention example, the area ratio of the ferrite phase is in the range of 25 to 80%, and the total strain amount of continuous wire rolling (= ln (cross-sectional area before rolling / cross-sectional area after rolling)) is 6.5 or less, In addition, by controlling the finish rolling speed to 85 m / s or less and accurately controlling the finish rolling temperature to 1000 ° C. or more (condition (a)), one hot wire rod rolling from the billet without generating surface flaws. Can produce a large single coil with a small diameter of φ8 mm or less and a weight of 400 kg or more.
一方、比較例Ｎｏ．２０，２６では、ビレット断面積が小さく、単重が４００ｋｇ未満と小さいために、従来の特殊なミニミルと同様に通常の線材圧延にて割れなく線材圧延が可能であるが、生産性・経済性・納期に劣るため意味がない。
比較例Ｎｏ．２１，２７では、製品の線径が大きく、連続線材圧延での総歪み量が小さいために、通常の線材圧延で割れなく圧延可能であるが、その後の伸線・焼鈍工程の負荷が大きく、経済性・納期に劣るため意味がない。
比較例Ｎｏ．２３，２５では、製品の線径が小さいため、連続線材圧延での総歪み量が大きいために、仕上げ圧延にて剪断割れが発生している。
比較例Ｎｏ．２２，２４，Ｎｏ．２８〜３０では、通常の線材圧延工程にて連続線材圧延を施しているが、本発明例に対して、前記本発明例の(a)条件を満たしておらず、表面疵が多発しており、表面疵がない大単重の熱間圧延線材が得られていない。
比較例Ｎｏ．３１〜３４では、汎用のＳＵＳ３０４およびＳＵＳ４３０系の成分で、フェライト相の面積率が２５〜８０％を外れており、通常の連続線材圧延にて疵が発生することなく大単重で圧延可能であり、本発明の効果の優位性が無い。
以上の実施例から本発明における連続線材圧延条件を正確に制御された２相ステンレス鋼線材の大単重熱間圧延線材コイルの優位性は明らかである。
On the other hand, Comparative Example No. In No. 20 and 26, the billet cross-sectional area is small and the unit weight is as small as less than 400 kg, so that the wire rod can be rolled without cracking by ordinary wire rod rolling as with the conventional special mini mill.・ Because it is inferior in delivery date, it is meaningless.
Comparative Example No. 21 and 27, because the product has a large wire diameter and a small total strain amount in continuous wire rolling, it can be rolled without cracking in ordinary wire rolling, but the load of the subsequent wire drawing and annealing process is large. There is no point because it is inferior in economic efficiency and delivery.
Comparative Example No. In Nos. 23 and 25, since the wire diameter of the product is small, the total strain amount in continuous wire rolling is large, so that shear cracks are generated in finish rolling.
Comparative Example No. 22, 24, no. In 28-30, continuous wire rolling is performed in a normal wire rod rolling process, but with respect to the present invention example, the condition (a) of the present invention example is not satisfied, and surface flaws occur frequently. No large single-piece hot-rolled wire with no surface defects has been obtained.
Comparative Example No. Nos. 31 to 34 are general-purpose SUS304 and SUS430 components, and the ferrite phase area ratio is out of 25 to 80%, and can be rolled with a large unit weight without generating wrinkles in normal continuous wire rolling. There is no superiority of the effect of the present invention.
From the above examples, the superiority of the large single-heavy hot-rolled wire coil of the duplex stainless steel wire in which the continuous wire-rolling conditions in the present invention are accurately controlled is clear.
以上の各実施例から明らかなように、本発明により、２相ステンレス鋼線材において、４００ｋｇ以上の大単重の細径線材を安定して低コストに提供できるため、２相ステンレス鋼線の市場への適用比率を大幅に向上することができ、産業上極めて有用である。
As is clear from each of the above examples, according to the present invention, in the duplex stainless steel wire, a large single-weight thin wire having a weight of 400 kg or more can be stably provided at a low cost. The application ratio can be greatly improved, which is extremely useful in the industry.
Claims (2)
Contains 1% or more of Mo; 6.0% or less, Cu; 4.0% or less, W; 1.0% or less, Nb; 1.0% or less, Ti; 1.0% or less. The hot-rolled wire rod according to claim 1, wherein:
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| US20120009433A1 (en) * | 2009-03-19 | 2012-01-12 | Masaharu Hatano | Duplex stainless steel sheet with excellent press-formability |
| CN103348023A (en) * | 2011-02-08 | 2013-10-09 | 新日铁住金不锈钢株式会社 | Hot rolled ferritic stainless steel sheet, method for producing same, and method for producing ferritic stainless steel sheet |
| CN103469051A (en) * | 2013-08-16 | 2013-12-25 | 广东华鳌合金新材料有限公司 | Duplex stainless steel master alloy and preparation method thereof |
| KR101419878B1 (en) | 2012-12-24 | 2014-07-15 | 주식회사 포스코 | Method for cold rolling for duplex stainless steel |
| JP2015168905A (en) * | 2014-03-07 | 2015-09-28 | セイコーインスツル株式会社 | Stainless steel metal fiber, and method for producing stainless steel metal fiber |
| JP2015218378A (en) * | 2014-05-20 | 2015-12-07 | 日本精線株式会社 | Two-phase system stainless steel wire excellent in magnetic property and magnetic wire gauze product using the same |
| CN109321836A (en) * | 2018-12-06 | 2019-02-12 | 江苏合众不锈钢有限公司 | A kind of section nickel novel low-carbon austenic stainless steel belt and preparation method thereof |
| CN109554633A (en) * | 2018-12-25 | 2019-04-02 | 成都永益泵业股份有限公司 | The preparation method of resistant material and phosphoric acid material pulp pump |
| JP2021031757A (en) * | 2019-08-29 | 2021-03-01 | 日鉄ステンレス株式会社 | Two-phase stainless steel wire material and two-phase stainless steel wire and chain |
| CN112853209A (en) * | 2020-12-31 | 2021-05-28 | 江苏永钢集团有限公司 | Zr-containing welding wire steel hot-rolled wire rod and production process thereof |
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| US20120009433A1 (en) * | 2009-03-19 | 2012-01-12 | Masaharu Hatano | Duplex stainless steel sheet with excellent press-formability |
| US9399809B2 (en) | 2011-02-08 | 2016-07-26 | Nippon Steel & Sumikin Stainless Steel Corporation | Hot rolled ferritic stainless steel sheet, method for producing same, and method for producing ferritic stainless steel sheet |
| CN103348023A (en) * | 2011-02-08 | 2013-10-09 | 新日铁住金不锈钢株式会社 | Hot rolled ferritic stainless steel sheet, method for producing same, and method for producing ferritic stainless steel sheet |
| CN103348023B (en) * | 2011-02-08 | 2015-11-25 | 新日铁住金不锈钢株式会社 | The manufacture method of ferrite-group stainless steel hot-rolled steel sheet and manufacture method and ferrite series stainless steel plate |
| US10072323B2 (en) | 2011-02-08 | 2018-09-11 | Nippon Steel & Sumikin Stainless Steel Corporation | Hot rolled ferritic stainless steel sheet, method for producing same, and method for producing ferritic stainless steel sheet |
| KR101419878B1 (en) | 2012-12-24 | 2014-07-15 | 주식회사 포스코 | Method for cold rolling for duplex stainless steel |
| CN103469051A (en) * | 2013-08-16 | 2013-12-25 | 广东华鳌合金新材料有限公司 | Duplex stainless steel master alloy and preparation method thereof |
| JP2015168905A (en) * | 2014-03-07 | 2015-09-28 | セイコーインスツル株式会社 | Stainless steel metal fiber, and method for producing stainless steel metal fiber |
| JP2015218378A (en) * | 2014-05-20 | 2015-12-07 | 日本精線株式会社 | Two-phase system stainless steel wire excellent in magnetic property and magnetic wire gauze product using the same |
| CN109321836A (en) * | 2018-12-06 | 2019-02-12 | 江苏合众不锈钢有限公司 | A kind of section nickel novel low-carbon austenic stainless steel belt and preparation method thereof |
| CN109554633A (en) * | 2018-12-25 | 2019-04-02 | 成都永益泵业股份有限公司 | The preparation method of resistant material and phosphoric acid material pulp pump |
| CN109554633B (en) * | 2018-12-25 | 2020-04-10 | 成都永益泵业股份有限公司 | Corrosion-resistant material and preparation method of phosphoric acid slurry pump |
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| JP7349849B2 (en) | 2019-08-29 | 2023-09-25 | 日鉄ステンレス株式会社 | chain |
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