JP4519513B2 - High-strength stainless steel wire with excellent rigidity and manufacturing method thereof - Google Patents
High-strength stainless steel wire with excellent rigidity and manufacturing method thereof Download PDFInfo
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- 229910001220 stainless steel Inorganic materials 0.000 title claims description 35
- 238000004519 manufacturing process Methods 0.000 title claims description 23
- 238000005491 wire drawing Methods 0.000 claims description 64
- 229910000831 Steel Inorganic materials 0.000 claims description 27
- 239000010959 steel Substances 0.000 claims description 27
- 229910000734 martensite Inorganic materials 0.000 claims description 18
- 230000032683 aging Effects 0.000 claims description 17
- 239000000463 material Substances 0.000 claims description 16
- 238000000034 method Methods 0.000 claims description 14
- 238000010438 heat treatment Methods 0.000 claims description 10
- 229910052799 carbon Inorganic materials 0.000 claims description 9
- 229910052748 manganese Inorganic materials 0.000 claims description 9
- 229910052759 nickel Inorganic materials 0.000 claims description 9
- 229910052757 nitrogen Inorganic materials 0.000 claims description 9
- 238000001816 cooling Methods 0.000 claims description 7
- 229910000963 austenitic stainless steel Inorganic materials 0.000 claims description 6
- 239000010935 stainless steel Substances 0.000 claims description 6
- 229910052782 aluminium Inorganic materials 0.000 claims description 5
- 229910052802 copper Inorganic materials 0.000 claims description 5
- 229910052758 niobium Inorganic materials 0.000 claims description 5
- 229910052719 titanium Inorganic materials 0.000 claims description 4
- 229910052715 tantalum Inorganic materials 0.000 claims description 3
- 229910052726 zirconium Inorganic materials 0.000 claims description 3
- 229910052720 vanadium Inorganic materials 0.000 claims description 2
- 229910052804 chromium Inorganic materials 0.000 claims 4
- 230000000694 effects Effects 0.000 description 19
- 230000000052 comparative effect Effects 0.000 description 8
- 238000012360 testing method Methods 0.000 description 7
- 230000001965 increasing effect Effects 0.000 description 6
- 239000000047 product Substances 0.000 description 6
- 230000007423 decrease Effects 0.000 description 5
- 239000000203 mixture Substances 0.000 description 5
- 229910001566 austenite Inorganic materials 0.000 description 4
- 238000010622 cold drawing Methods 0.000 description 4
- 229920006395 saturated elastomer Polymers 0.000 description 4
- 239000000126 substance Substances 0.000 description 4
- 238000005336 cracking Methods 0.000 description 3
- 229910000975 Carbon steel Inorganic materials 0.000 description 2
- 238000000137 annealing Methods 0.000 description 2
- 239000010962 carbon steel Substances 0.000 description 2
- 238000005260 corrosion Methods 0.000 description 2
- 230000007797 corrosion Effects 0.000 description 2
- 230000005415 magnetization Effects 0.000 description 2
- 229910052750 molybdenum Inorganic materials 0.000 description 2
- 238000012545 processing Methods 0.000 description 2
- 238000005728 strengthening Methods 0.000 description 2
- CURLTUGMZLYLDI-UHFFFAOYSA-N Carbon dioxide Chemical compound O=C=O CURLTUGMZLYLDI-UHFFFAOYSA-N 0.000 description 1
- 229910000639 Spring steel Inorganic materials 0.000 description 1
- 229910045601 alloy Inorganic materials 0.000 description 1
- 239000000956 alloy Substances 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 235000011089 carbon dioxide Nutrition 0.000 description 1
- 230000001276 controlling effect Effects 0.000 description 1
- 238000012937 correction Methods 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 230000000593 degrading effect Effects 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 230000002708 enhancing effect Effects 0.000 description 1
- 230000004907 flux Effects 0.000 description 1
- 229910052739 hydrogen Inorganic materials 0.000 description 1
- 239000001257 hydrogen Substances 0.000 description 1
- 125000004435 hydrogen atom Chemical class [H]* 0.000 description 1
- 230000006698 induction Effects 0.000 description 1
- 238000011835 investigation Methods 0.000 description 1
- 238000005259 measurement Methods 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 150000004767 nitrides Chemical class 0.000 description 1
- 238000000399 optical microscopy Methods 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 239000000700 radioactive tracer Substances 0.000 description 1
- 238000007670 refining Methods 0.000 description 1
- 230000001105 regulatory effect Effects 0.000 description 1
- 238000009864 tensile test Methods 0.000 description 1
- 229910052721 tungsten Inorganic materials 0.000 description 1
- 238000010792 warming Methods 0.000 description 1
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 1
- 229910000859 α-Fe Inorganic materials 0.000 description 1
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Description
本発明は高強度ステンレス鋼線に関わり、さらに詳しくは高強度オーステナイト系ステンレス鋼線の剛性率向上技術に関するものである。 The present invention relates to a high-strength stainless steel wire, and more particularly to a technique for improving the rigidity of a high-strength austenitic stainless steel wire.
従来、ばね用等の高強度ステンレス鋼線は、冷間伸線加工時の縦割れ(時効割れ)が問題であり、成分,水素量や伸線加工後の加工誘起マルテンサイト量を規制して防止する技術が提案されている(特許文献1)。 Conventionally, high-strength stainless steel wires for springs, etc., have had problems with longitudinal cracks (aging cracks) during cold drawing, and the amount of components, hydrogen, and the amount of work-induced martensite after wire drawing are regulated. A technique for preventing this has been proposed (Patent Document 1).
また、鉄鋼材料の強靱化技術に関して、熱間または温間でオーステナイト組織を加工後に冷却させてマルテンサイト変態させるオースフォーム手法が、炭素鋼で古くから検討されてきた(例えば非特許文献1)。しかし、熱間や温間域でオーステナイト組織を加工した直後に焼入れしなければならいため、制約が大きく、工業的には殆ど普及していない。 Further, regarding the toughening technology of steel materials, an ausforming method in which an austenite structure is cooled after being processed hot or warm and then transformed into martensite has been studied for a long time with carbon steel (for example, Non-Patent Document 1). However, since the austenite structure must be quenched immediately after being processed in a hot or warm region, the restrictions are great, and it is hardly spread industrially.
一方、最近、結晶粒微細化や常温の伸線加工によるオースフォームの強靱化効果を使うことで、延靱性と弾性率を著しく向上させた高強度ステンレス鋼線が提案されている(特許文献2)。 On the other hand, recently, a high-strength stainless steel wire has been proposed in which ductility and elastic modulus are remarkably improved by using the effect of toughening ausfoam by grain refinement or wire drawing at room temperature (Patent Document 2). ).
また、伸線温度を温間に制御することで非常に高い強度のステンレス鋼線が得られることも提案されている(特許文献3)。 It has also been proposed that a stainless steel wire with very high strength can be obtained by controlling the wire drawing temperature warmly (Patent Document 3).
従来、ステンレス鋼線の強度と弾性率を高める技術が提案されてきたが、本発明では、更に、ステンレス鋼線の剛性率を飛躍的に向上させ、炭素鋼であるピアノ線並の剛性率を高強度ステンレス鋼線で安定して得ることにある。 Conventionally, techniques for increasing the strength and elastic modulus of stainless steel wires have been proposed. However, in the present invention, the rigidity of stainless steel wires has been dramatically improved to achieve the same rigidity as that of piano wires that are carbon steel. It is to obtain stably with a high-strength stainless steel wire.
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、オーステナイト系ステンレス鋼において、剛性率を下げるNi等の合金元素の添加量を極力抑制して、温度制御による温間伸線加工を施し、更には低温時効処理を組み合わすことで、加工誘起マルテンサイト組織を制御し、延靱性・伸線加工性を劣化させることなく、高強度ステンレス鋼線の剛性率を著しく向上させることを見出した。 As a result of various studies to solve the above problems, the present inventors have suppressed the addition amount of alloy elements such as Ni, which lowers the rigidity, as much as possible in austenitic stainless steel, and performed warm drawing by temperature control. In addition, by combining low temperature aging treatment, the work-induced martensite structure is controlled, and the rigidity of high-strength stainless steel wire is significantly improved without degrading ductility and wire drawing workability. I found it.
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:0.03〜0.14%,Si:0.1〜4.0%,Mn:0.1〜5.0%,Ni:2.0〜8.0%,Cr:13.0〜19.0%,N:0.005〜0.21%を含有し残部がFeおよび不可避的な成分からなり、且つ、(1)式で表されるMd30の値が25〜150(℃)である線材又は鋼線を70〜400℃の温間域に加熱して合計減面率:40〜95%の伸線加工を施すことを特徴とする剛性率に優れた高強度ステンレス鋼線の製造方法である。
Md30=551−462(C+N)−9.2Si−8.1Mn
−29(Ni+Cu)−13.7Cr−18.5Mo ・・・・・・・(1)
(2)質量%で、C:0.03〜0.14%,Si:0.1〜4.0%,Mn:0.1〜5.0%,Ni:2.0〜8.0%,Cr:13.0〜19.0%,N:0.005〜0.21%を含有し残部がFeおよび不可避的な成分からなり、且つ、(1)式で表されるMd30の値が25〜100(℃)である線材又は鋼線を70〜400℃の温間域に加熱して合計減面率:20〜75%の伸線加工を施し、引き続き、冷却して100℃以下で合計減面率:10〜44%の伸線加工を施すことを特徴とする剛性率に優れる高強度ステンレス鋼線の製造方法である。
(3)質量%で、C:0.03〜0.14%,Si:0.1〜4.0%,Mn:0.1〜8.0%,Ni:1.0〜8.0%,Cr:13.0〜19.0%,N:0.005〜0.30%を含有し残部がFeおよび不可避的な成分からなり、且つ、(1)式で表されるMd30の値が0〜150(℃)である線材又は鋼線を50〜400℃の温間域に加熱して合計減面率:40〜95%の伸線加工を施し、その後、150〜600℃の範囲で低温時効を施すことを特徴とする剛性率に優れた高強度ステンレス鋼線の製造方法である。
(4)質量%で、C:0.03〜0.14%,Si:0.1〜4.0%,Mn:0.1〜8.0%,Ni:1.0〜8.0%,Cr:13.0〜19.0%,N:0.005〜0.30%を含有し残部がFeおよび不可避的な成分からなり、且つ、(1)式で表されるMd30の値が0〜100(℃)である線材又は鋼線を50〜400℃の温間域に加熱して合計減面率:20〜75%の伸線加工を施し、引き続き、冷却して100℃以下の低温域で合計減面率:10〜44%の伸線加工を施し、その後、150〜600℃の範囲で低温時効を施すことを特徴とする剛性率に優れる高強度ステンレス鋼線の製造方法である。
(5)さらに、質量%で、0.01〜0.30%のAl,Nb,Ti,Zr,Ta、又はWのいずれか1種または2種以上及び/又は、0.05〜0.5%のVを含有することを特徴とする前記(1)〜(4)記載の剛性率に優れる高強度ステンレス鋼線の製造方法である。
(6)さらに、質量%で、Mo:0.1〜3.0%,Cu:0.1〜3.0%,Co:0.05〜3.0%のいずれか1種又は2種以上を含有することを特徴とする前記(1)〜(5)記載の剛性率に優れる高強度ステンレス鋼線の製造方法である。
(7)さらに、質量%で、Ca:0.0005〜0.01%,Mg:0.0005〜0.01%の1種以上を含有することを特徴とする前記(1)〜(6)記載の剛性率に優れる高強度ステンレス鋼線の製造方法である。
(8)さらに、質量%で、B:0.001〜0.01%を含有することを特徴とする前記(1)〜(7)記載の剛性率に優れる高強度ステンレス鋼線の製造方法である。
(9)前記(1)〜(8)記載の製造方法で製造されたステンレス鋼線で、引張強さが2000〜3500N/mm2、加工誘起マルテンサイト量が20〜80%,剛性率が70GPa以上であることを特徴とする剛性率に優れる高強度ステンレス鋼線である。
(10)前記(9)記載の鋼線の素材となる伸線加工用の準安定オーステナイト系ステンレス鋼線材である。
That is, the gist of the present invention is as follows.
(1) By mass%, C: 0.03-0.14%, Si: 0.1-4.0%, Mn: 0.1-5.0%, Ni: 2.0-8.0% , Cr: 13.0 to 19.0%, N: 0.005 to 0.21%, the balance being Fe and inevitable components, and the value of Md30 represented by the formula (1) is Heating a wire or steel wire of 25 to 150 (° C.) in a warm region of 70 to 400 ° C. and performing a drawing process with a total area reduction ratio of 40 to 95% and excellent rigidity This is a method for producing a high-strength stainless steel wire.
Md30 = 551-462 (C + N) -9.2Si-8.1Mn
-29 (Ni + Cu) -13.7Cr-18.5Mo (1)
(2) By mass%, C: 0.03-0.14%, Si: 0.1-4.0%, Mn: 0.1-5.0%, Ni: 2.0-8.0% , Cr: 13.0 to 19.0%, N: 0.005 to 0.21%, the balance being Fe and inevitable components, and the value of Md30 represented by the formula (1) is A wire or steel wire having a temperature of 25 to 100 (° C.) is heated to a warm region of 70 to 400 ° C. to give a total area reduction ratio of 20 to 75 %, followed by cooling to 100 ° C. or less. Total area reduction ratio: It is a manufacturing method of the high strength stainless steel wire excellent in the rigidity characterized by performing a wire drawing process of 10 to 44 %.
(3) By mass%, C: 0.03-0.14%, Si: 0.1-4.0%, Mn: 0.1-8.0%, Ni: 1.0-8.0% , Cr: 13.0 to 19.0%, N: 0.005 to 0.30%, with the balance being Fe and inevitable components, and the value of Md30 represented by the formula (1) is A wire or steel wire having a temperature of 0 to 150 (° C.) is heated to a warm region of 50 to 400 ° C. to give a total area reduction ratio of 40 to 95%. A method for producing a high-strength stainless steel wire having excellent rigidity, characterized by being subjected to low temperature aging.
(4) By mass%, C: 0.03 to 0.14%, Si: 0.1 to 4.0%, Mn: 0.1 to 8.0%, Ni: 1.0 to 8.0% , Cr: 13.0 to 19.0%, N: 0.005 to 0.30%, with the balance being Fe and inevitable components, and the value of Md30 represented by the formula (1) is A wire rod or steel wire having a temperature of 0 to 100 (° C.) is heated to a warm region of 50 to 400 ° C. to give a total area reduction ratio of 20 to 75 %, followed by cooling to 100 ° C. A method for producing a high-strength stainless steel wire excellent in rigidity, characterized by subjecting a total area reduction ratio of 10 to 44 % in a low-temperature region to a low-temperature aging in a range of 150 to 600 ° C. is there.
(5) Further, 0.01% to 0.30% of Al, Nb, Ti, Zr, Ta, or W and / or 0.05 to 0.5% by mass. It is a manufacturing method of the high-strength stainless steel wire excellent in the rigidity of the said (1)-(4) description characterized by containing% V.
(6) Furthermore, by mass%, any one or more of Mo: 0.1 to 3.0%, Cu: 0.1 to 3.0%, Co: 0.05 to 3.0% It is a manufacturing method of the high strength stainless steel wire which is excellent in the rigidity of the said (1)-(5) description characterized by containing.
(7) The above (1) to (6), further comprising at least one of Ca: 0.0005 to 0.01% and Mg: 0.0005 to 0.01% by mass%. It is a manufacturing method of the high-strength stainless steel wire which is excellent in the described rigidity.
(8) The method for producing a high-strength stainless steel wire having excellent rigidity according to the above (1) to (7), further comprising B: 0.001 to 0.01% by mass%. is there.
(9) A stainless steel wire produced by the production method described in (1) to (8) above, having a tensile strength of 2000 to 3500 N / mm 2 , an amount of work-induced martensite of 20 to 80%, and a rigidity of 70 GPa. This is a high-strength stainless steel wire with excellent rigidity characterized by the above.
(10) A metastable austenitic stainless steel wire for wire drawing, which is a material for the steel wire according to (9).
本発明による高強度ステンレス鋼線は、高強度オーステナイト系ステンレス鋼線の剛性率を飛躍的に向上したものであり、ステンレス鋼ばねで、ピアノ線のばねに匹敵するばね定数を得ることにある。 The high-strength stainless steel wire according to the present invention is a material in which the rigidity of a high-strength austenitic stainless steel wire is dramatically improved, and is to obtain a spring constant comparable to that of a piano wire with a stainless steel spring.
以下に、先ず、請求項1の限定理由について述べる。 The reason for limitation of claim 1 will be described first.
Cは伸線加工後に高強度を得るために、0.03%以上(以下は全て質量%)添加する。しかし、0.14%を超えて添加すると、粒界に粗大Cr炭化物が析出し、延靱性が低下することから、上限を0.14%とする。好ましい範囲は、0.06〜0.12%である。 C is added in an amount of 0.03% or more (the following are all mass%) in order to obtain high strength after wire drawing. However, if added over 0.14%, coarse Cr carbide precipitates at the grain boundaries and ductility decreases, so the upper limit is made 0.14%. A preferable range is 0.06 to 0.12%.
Siは脱酸のため、0.1%以上添加する。しかし、4.0%を超えて添加するとその効果は飽和するばかりか、製造性が悪く、また、逆に延靱性が劣化するため、上限を4.0%以下に限定する。好ましい範囲は、0.5〜2.0%である。 Si is added in an amount of 0.1% or more for deoxidation. However, if the addition exceeds 4.0%, the effect is not only saturated, but the manufacturability is poor, and conversely the ductility deteriorates, so the upper limit is limited to 4.0% or less. A preferable range is 0.5 to 2.0%.
Mnは脱酸のため、0.1%以上添加する。しかし、5.0%を超えて添加すると、剛性率が低下するため、上限を5.0%に限定する。好ましい範囲は、0.5〜2.0%である。 Mn is added at 0.1% or more for deoxidation. However, if added over 5.0%, the rigidity decreases, so the upper limit is limited to 5.0%. A preferable range is 0.5 to 2.0%.
Niは、延靱性を確保するため、2.0%以上添加する。しかし、8.0%を超えて添加すると、強度が低下するばかりか剛性率も低下するため、上限を8.0%に限定する。好ましい範囲は、4.0〜7.0%である。 Ni is added in an amount of 2.0% or more in order to ensure ductility. However, if added over 8.0%, the strength is lowered and the rigidity is also lowered, so the upper limit is limited to 8.0%. A preferable range is 4.0 to 7.0%.
Crは、耐食性を確保するため、13.0%以上添加する。しかし、19.0%を超えて添加すると、延靱性が劣化するため、上限を19.0%に限定する。好ましい範囲は、14.0〜18.0%である。 Cr is added in an amount of 13.0% or more to ensure corrosion resistance. However, if added over 19.0%, ductility deteriorates, so the upper limit is limited to 19.0%. A preferable range is 14.0 to 18.0%.
Nは伸線加工後に高強度を得るために、0.005%以上添加する。しかし、0.21%を超えて添加すると、製造時にブローホールが生成し、製造性を著しく劣化させるため、上限を0.21%に限定する。好ましい範囲は、0.05〜0.18%のである。 N is added in an amount of 0.005% or more in order to obtain high strength after wire drawing. However, if added over 0.21%, blowholes are produced during production, and the manufacturability is significantly deteriorated, so the upper limit is limited to 0.21%. A preferable range is 0.05 to 0.18%.
前記(1)式で規定されるMd30は、温間伸線加工後の加工誘起マルテンサイト量に影響を及ぼし、温間でのオースフォーム効果を発揮(延靱性を確保)して断線・縦割れ等の破壊無く高強度化・高剛性率化するため、25℃以上とする。しかしながら、150℃を超えると温間伸線でもオースフォームの効果が小さく、伸線加工により断線・縦割れ等の破壊が生じるため上限を150℃に限定する。好ましい範囲は、40〜100℃である。 Md30 defined by the above formula (1) affects the amount of work-induced martensite after warm wire drawing, exhibits the ausfoam effect in the warm state (ensures ductility), and breaks / longitudinal cracks. In order to achieve high strength and high rigidity without breakage, etc., the temperature should be 25 ° C or higher. However, if the temperature exceeds 150 ° C., the effect of ausforming is small even with warm wire drawing, and the upper limit is limited to 150 ° C. because breakage such as disconnection and vertical cracking occurs by wire drawing. A preferred range is 40-100 ° C.
温間伸線温度は、加工誘起マルテンサイト量・組織を制御し、低靱性の原因となる加工誘起マルテンサイト組織のセル化を抑制して断線・縦割れ等の破壊なく高強度化するため、少なくとも伸線前に70℃以上に加熱して伸線開始する。しかしながら、400℃以上に加熱すると、逆に加工誘起マルテンサイト量が抑制されて強度がでなくなる。そのため、上限を400℃とした。好ましい範囲は、100℃〜300℃である。また、加熱は通電式加熱,誘導加熱,雰囲気加熱等で実施する。 Warm wire drawing temperature controls the amount and structure of work-induced martensite, suppresses the cell formation of work-induced martensite structure that causes low toughness, and increases the strength without breakage such as disconnection and vertical cracking. Heat at least 70 ° C. before drawing to start drawing. However, when heated to 400 ° C. or higher, the amount of work-induced martensite is constrained and the strength is lost. Therefore, the upper limit was set to 400 ° C. A preferred range is 100 ° C to 300 ° C. Heating is performed by energization heating, induction heating, atmosphere heating, or the like.
温間での伸線減面率は、高強度化のため、少なくとも40%以上にする。しかしながら、95%以上伸線すると、延靱性が低下し、断線・縦割れ等の破壊が生じやすくなる。そのため、上限を95%とする。好ましい範囲は、50〜80%である。 In order to increase the strength, the wire drawing area reduction rate during warming is at least 40% or more. However, when wire drawing is 95% or more, ductility is lowered and breakage such as disconnection and vertical cracking is likely to occur. Therefore, the upper limit is set to 95%. A preferable range is 50 to 80%.
次に請求項2の限定理由について述べる。 Next, the reason for limitation of claim 2 will be described.
伸線前段で温間伸線を行い、伸線後段で100℃以下(伸線開始温度)の低温伸線を行うと、オースフォームの効果がより一層高まる。好ましい伸線開始温度は、−10〜80℃が経済的に好ましい。この時、伸線前段の温間の伸線減面率が20%未満なら、オースフォームの効果が不十分であり、伸線後段の低温伸線で加工誘起マルテンサイト組織がセル化するため破壊が生じる。一方、伸線前段の伸線減面率が90%超でも、延靱性が低下し、伸線後段の低温伸線で破壊が生じる。従って、伸線前段の温間伸線での伸線減面率を20〜90%に限定する。好ましい範囲は、30〜80%である。ここでの伸線後段の低温伸線とは、例えば、(1)1台の連続伸線機内において、前段を加熱装置により温間伸線し、後段を加熱無し、または、ドラム冷却強化,冷風,ドライアイス等により冷却強化して低温域で伸線加工する,(2)1台の単釜伸線機および連続伸線機で温間伸線を行った後に別の伸線機で低温伸線を行うことを意味する。 If the warm drawing is performed before the drawing and the low temperature drawing at 100 ° C. or less (the drawing start temperature) is performed after the drawing, the effect of the ausfoam is further enhanced. A preferred wire drawing start temperature is economically preferably from −10 to 80 ° C. At this time, if the warm drawing area reduction ratio before the wire drawing is less than 20%, the effect of ausforming is insufficient, and the work-induced martensite structure becomes a cell at the low temperature drawing after the wire drawing. Occurs. On the other hand, even if the drawing area reduction ratio before the drawing is more than 90%, the ductility decreases, and fracture occurs at the low temperature drawing after the drawing. Therefore, the drawing area reduction rate in the warm drawing before drawing is limited to 20 to 90%. A preferable range is 30 to 80%. The low temperature wire drawing after the wire drawing here is, for example, (1) In one continuous wire drawing machine, the front stage is warm drawn by a heating device and the rear stage is not heated, or the drum cooling is strengthened, cold air , Cooling and strengthening with dry ice etc. and drawing in low temperature range (2) Warm drawing with one single pot drawing machine and continuous drawing machine and then drawing with low temperature drawing with another drawing machine Means to do a line.
また、伸線後段の低温伸線において、伸線減面率が10%未満ならオースフォームの効果が小さく、あまり意味がない。一方、70%超なら加工誘起マルテンサイト組織がセル化して延靱性が低下する。従って、伸線後段の低温伸線での減面率を10〜70%に限定する。好ましい範囲は、20〜60%である。 Moreover, in the low temperature wire drawing after wire drawing, if the wire drawing area reduction rate is less than 10%, the effect of ausfoam is small, which is not very meaningful. On the other hand, if it exceeds 70%, the work-induced martensite structure becomes a cell and the ductility is lowered. Therefore, the area reduction rate at the low temperature drawing after the drawing is limited to 10 to 70%. A preferable range is 20 to 60%.
次に請求項3,4の限定理由について述べる。 Next, the reasons for limitation of claims 3 and 4 will be described.
伸線後に低温焼鈍を行うことで、強度と剛性率が更に向上するため、請求項1および2の成分範囲を拡大することができる。 By performing low-temperature annealing after wire drawing, the strength and rigidity are further improved, so that the component range of claims 1 and 2 can be expanded.
Niは、Mn量の上限を広げることで下限を1.0%に拡大することができる。 Ni can expand a minimum to 1.0% by extending the upper limit of the amount of Mn.
Mn量は、最後に低温時効を行うことで上限を8.0%に拡大することができる。 The upper limit of the amount of Mn can be expanded to 8.0% by finally performing low temperature aging.
Nは、Nの溶解量を増加させるMn量を増やすことで上限を0.30%まで拡大することができる。特に低温時効時にCr窒化物を析出させて高強度および高剛性率化に有効である。しかし、この場合でも0.30%を超えて添加すると、製造時にブローホールが生成し、製造性を著しく劣化させるため、上限を0.30%に限定する。 The upper limit of N can be increased to 0.30% by increasing the amount of Mn that increases the amount of N dissolved. In particular, Cr nitride is precipitated during low temperature aging, which is effective for increasing strength and rigidity. However, even in this case, if added over 0.30%, blowholes are generated during production, and the manufacturability is significantly deteriorated, so the upper limit is limited to 0.30%.
Md30の値は、低温時効を行うことで剛性率が向上するため、下限を0℃まで拡大することができる。 The value of Md30 can be expanded to a lower limit of 0 ° C. because the rigidity is improved by performing low temperature aging.
温間域での伸線加工の加熱温度は、低温時効による強度および剛性率向上のため、下限を50℃まで拡大することができる。 The lower limit of the heating temperature for wire drawing in the warm region can be increased to 50 ° C. in order to improve the strength and rigidity by low temperature aging.
時効温度は、150℃未満では高強度・高剛性の効果が小さいため150℃以上に限定する。一方、600℃を超えると強度が低下するため、上限を600℃に限定する。好ましい範囲は、250〜500℃である。 When the aging temperature is less than 150 ° C., the effect of high strength and high rigidity is small, so it is limited to 150 ° C. or more. On the other hand, if the temperature exceeds 600 ° C., the strength decreases, so the upper limit is limited to 600 ° C. A preferred range is 250-500 ° C.
次に請求項5の限定理由について述べる。 Next, the reason for limitation of claim 5 will be described.
Al,Nb,Ti,Zr,Ta,Wは、微細な炭窒化物を形成し、鋼線の溶体化処理後のオーステナイト結晶粒を安定的に微細化させて延靱性を維持しつつ高強度化させるため、必要に応じて、そのいずれかを0.01%以上添加することが望ましい。しかし、0.30%を超えて添加してもその効果は飽和し、経済的でないばかりか、逆に延靱性を低下させるため、上限を0.3%とすることが望ましい。また、これら元素の複数を添加する場合にあってもその上限は0.35%、望ましくは0.30%にとどまるのがよい。 Al, Nb, Ti, Zr, Ta, and W form fine carbonitrides, increase the strength while maintaining ductility by stably refining austenite grains after solution treatment of steel wire Therefore, it is desirable to add any one of 0.01% or more as necessary. However, even if added over 0.30%, the effect is saturated and not only economical, but conversely lowers the toughness, so the upper limit is preferably made 0.3%. Further, even when a plurality of these elements are added, the upper limit is 0.35%, preferably 0.30%.
特に、AlおよびNbにおいては、熱間加工性を向上させるとともに、析出強化による高強度化に寄与することから有効である。 In particular, Al and Nb are effective because they improve hot workability and contribute to high strength by precipitation strengthening.
Vは微細な炭窒化物を形成し、鋼線の溶体化処理後のオーステナイト結晶粒を安定的に微細化させて延靱性を維持しつつ高強度化させるため、必要に応じ、0.05%以上添加する。しかし、0.5%を超えて添加してもその効果は飽和するし、逆に延靱性を低下させるため、上限を0.5%とすることが望ましい。また、このVは前記したAlやNb,Tiなどのグループの組成と併用して添加してもよい。 V forms a fine carbonitride and stably refines the austenite crystal grains after solution treatment of the steel wire to increase the strength while maintaining ductility. Add more. However, even if added over 0.5%, the effect is saturated, and conversely the ductility is lowered. Therefore, the upper limit is preferably made 0.5%. Further, this V may be added in combination with the above-described group composition such as Al, Nb, and Ti.
次に、請求項6記載の限定理由について述べる。
Cu,Mo,Coは、耐食性に有効であるため、必要に応じ、Cu;0.1%以上,Mo;0.1%以上,Co;0.05%以上添加する。しかし、3.0%を超えて添加してもその効果は飽和するし、Cu,Moについては逆に剛性率が低下するため、上限を3.0%にする。好ましい範囲は、それぞれ、Mo;0.5〜2.5%,Cu:0.3〜2.5%,Co;0.1〜2.0%である。
Next, the reason for limitation described in claim 6 will be described.
Since Cu, Mo, and Co are effective for corrosion resistance, Cu; 0.1% or more, Mo; 0.1% or more, Co; 0.05% or more is added as necessary. However, even if added over 3.0%, the effect is saturated, and the rigidity of Cu and Mo is conversely lowered, so the upper limit is made 3.0%. Preferable ranges are Mo: 0.5 to 2.5%, Cu: 0.3 to 2.5%, Co; 0.1 to 2.0%, respectively.
次に、請求項7記載の限定理由について述べる。
Ca,Mgは、必要に応じて、脱酸を強化することを目的に、それぞれ、Ca;0.0005%〜0.01%,Mg;0.0005〜0.01%添加する。ここで、過剰に添加すると粗大な脱酸生成物により延靱性が劣化するため、それぞれ、上限を設定する。好ましい範囲は、Ca:0.001〜0.005%,Mg;0.001〜0.005%である。
Next, the reason for limitation described in claim 7 will be described.
If necessary, Ca and Mg are added respectively for Ca; 0.0005% to 0.01% and Mg; 0.0005 to 0.01% for the purpose of enhancing deoxidation. Here, since the ductility deteriorates due to a coarse deoxidation product when added in excess, an upper limit is set for each. Preferred ranges are Ca: 0.001 to 0.005%, Mg; 0.001 to 0.005%.
次に、請求項8記載の限定理由について述べる。
Bは、熱間加工性確保のために、必要に応じて、0.001%以上添加する。しかしながら、0.01%を超えて添加してもボライドを生成し、縦割れや破断等、伸線加工性が劣化するため上限を0.01%とする。好ましい範囲は、0.002〜0.008%である。
Next, the reason for limitation described in claim 8 will be described.
B is added in an amount of 0.001% or more as necessary to ensure hot workability. However, even if added over 0.01%, boride is generated, and wire drawing workability such as vertical cracks and breakage deteriorates, so the upper limit is made 0.01%. A preferred range is 0.002 to 0.008%.
次に、請求項9記載の限定理由について述べる。 Next, the reason for limitation described in claim 9 will be described.
伸線加工後の引張強さが2000N/mm2未満の場合、基本的に延靱性が高いため、本発明の効果が顕著に現れない。それに対し、伸線加工後の引張強さが2000N/mm2以上の高強度材になると、延靱性が低下するため、温間伸線によるオースフォーム等の本発明の効果が明確となる。そのため、伸線加工後の引張強さが2000N/mm2以上に限定することが望ましい。一方、逆に過度に強度が高くなり過ぎると延靱性が著しく劣化し、経済的効果が小さくなるため、伸線加工後、又は低温時効処理後の強度の上限は3500N/mm2にすることが望ましい。好ましくは、2200〜3200N/mm2である。 When the tensile strength after wire drawing is less than 2000 N / mm 2 , the effect of the present invention does not appear remarkably because the ductility is basically high. On the other hand, when the tensile strength after wire drawing becomes a high strength material of 2000 N / mm 2 or more, the ductility decreases, and thus the effects of the present invention such as ausfoam by warm wire drawing become clear. Therefore, it is desirable to limit the tensile strength after wire drawing to 2000 N / mm 2 or more. On the other hand, if the strength is excessively increased, the ductility is remarkably deteriorated and the economic effect is reduced. Therefore, the upper limit of the strength after wire drawing or after low temperature aging treatment should be 3500 N / mm 2. desirable. Preferably, it is 2200-3200 N / mm < 2 >.
伸線加工後の加工誘起マルテンサイト量が20%未満の場合、通常の伸線加工後の引張強さが2000N/mm2未満となり、本発明の高延靱性の効果が顕著に現れず、また、剛性率も低くなる。そのため、加工誘起マルテンサイト量が20%以上であることが望ましい。一方、伸線加工後の加工誘起マルテンサイト量が80%を超えると加工誘起マルテンサイト組織が低延性のセル組織を示すようになり、素材の延靱性が低下する。そのため、上限を80%にすることが望ましい。 When the amount of work-induced martensite after wire drawing is less than 20%, the tensile strength after normal wire drawing is less than 2000 N / mm 2, and the effect of high ductility toughness of the present invention does not appear remarkably. Also, the rigidity becomes low. Therefore, it is desirable that the processing induced martensite amount is 20% or more. On the other hand, if the amount of work-induced martensite after wire drawing exceeds 80%, the work-induced martensite structure shows a low ductility cell structure, and the ductility of the material is lowered. Therefore, it is desirable that the upper limit be 80%.
尚、この加工誘起マルテンサイト量の測定は、例えば、直流磁化特性の測定装置などによる飽和磁束密度から求めることができる。また、簡易的なフェライトメータ等で測定する場合は、線径により補正が必要である。 In addition, the measurement of the amount of work-induced martensite can be obtained from the saturation magnetic flux density by, for example, a DC magnetization characteristic measuring device. Moreover, when measuring with a simple ferrite meter etc., correction | amendment is required by a wire diameter.
剛性率については、通常のSUS304引き抜き鋼線の場合、70GPa未満であるため、本発明範囲が70GPa未満では経済的効果が少ない。そのため、本発明では経済的効果が大きい70GPa以上に限定することが望ましい。なお、ここでの剛性率は低温焼鈍後の剛性率である。 As for the rigidity, in the case of a normal SUS304 drawn steel wire, it is less than 70 GPa, so if the range of the present invention is less than 70 GPa, the economic effect is small. Therefore, in this invention, it is desirable to limit to 70 GPa or more with a large economical effect. The rigidity here is the rigidity after low-temperature annealing.
以下に本発明の実施例についてさらに具体的に説明する。 Examples of the present invention will be described more specifically below.
本発明は、とりわけ、鋼線の目標特性として、引張強さが2000N/mm2以上,ばね用鋼線の剛性率が70GPa以上を有するものとし、鋼線製造性として縦割れおよび破断等の破壊が無いこととした。 In particular, the present invention assumes that the steel wire has the target properties of a tensile strength of 2000 N / mm 2 or more and the spring steel wire has a rigidity of 70 GPa or more. It was decided that there was no.
表1に示す化学組成の供試材は通常のステンレス線材の製造工程で溶製し、熱間でΦ5.5mmまで線材圧延を行い、1000℃で圧延を終了した。得られた線材を約1050℃の5minの熱処理を施し、水冷し、酸洗を施した。その後、φ3.0mmまで伸線加工を行い(1次伸線)、その後、ストランド炉にて1000℃の溶体化処理を施してばね用ステンレス鋼線の素材とした。そして、種々の条件(温間〜冷間)にて伸線加工(2次伸線)を施した。 The test materials having the chemical composition shown in Table 1 were melted in the normal manufacturing process of stainless steel wire, hot rolled to Φ5.5 mm, and finished at 1000 ° C. The obtained wire was heat-treated at about 1050 ° C. for 5 minutes, cooled with water, and pickled. Thereafter, wire drawing was performed to φ3.0 mm (primary wire drawing), and then a solution treatment at 1000 ° C. was performed in a strand furnace to obtain a spring stainless steel wire material. And wire drawing (secondary wire drawing) was performed under various conditions (warm to cold).
そして、この伸線加工後の製品の加工誘起マルテンサイト量,引張強さ,剛性率および伸線中の断線および鋼線製品の縦割れ(内部割れ等)の破壊の有無を調査した。 Then, the amount of work-induced martensite, the tensile strength, the rigidity, the wire breakage during wire drawing, and the presence or absence of vertical cracks (internal cracks, etc.) of steel wire products were investigated.
伸線加工後の加工誘起マルテンサイト量は、直流式のBHトレーサーにて飽和磁化を測定して求めた。
伸線加工後の引張強さは、JIS Z2241の引張試験により測定した。
伸線加工後の剛性率は、ねじり振り子法により測定した。
The amount of work-induced martensite after wire drawing was determined by measuring saturation magnetization with a direct current BH tracer.
The tensile strength after wire drawing was measured by a tensile test of JIS Z2241.
The rigidity after drawing was measured by the torsion pendulum method.
鋼線の破壊については、伸線加工中に断線が起こるか否かで判断し、縦割れ(内部割れ等)については、鋼線製品の10箇所から横断面に埋め込み研磨し、光学顕微鏡観察により割れの有無により判断した。 Steel wire breakage is determined by whether or not wire breakage occurs during wire drawing. Vertical cracks (internal cracks, etc.) are embedded and polished from 10 locations in the steel wire product into the cross section, and observed by optical microscopy. Judged by the presence or absence of cracks.
まず、本発明の基本成分の効果について述べる。ここで用いる供試材は前記工程による溶体化処理後の線材をφ3.0mmまで1次の伸線加工を施し、続いてAr雰囲気で溶体化処理を施して、その後、φ1.5mmまで2次伸線加工を施した。ここで、2次伸線加工は、温間伸線加工と温度制御伸線加工を施した。温間伸線では150℃に加熱後にφ1.5mmまで伸線加工を施し、温度制御伸線では伸線前段は180℃に加熱してφ2mm(減面率;約55%)まで伸線加工した後に常温まで冷却してφ1.5mmまで冷間で伸線加工を施した。まず、温間伸線加工の結果を表2,温度制御伸線加工の結果を表3に示す。 First, the effect of the basic component of the present invention will be described. The test material used here was subjected to the primary wire drawing to a diameter of φ3.0 mm after the solution treatment in the above process, followed by a solution treatment in an Ar atmosphere, and then to a secondary diameter of φ1.5 mm. Drawing process was performed. Here, the secondary wire drawing was performed by warm wire drawing and temperature-controlled wire drawing. In warm drawing, the wire was drawn to φ1.5 mm after heating to 150 ° C, and in the temperature-controlled drawing, the pre-drawing step was heated to 180 ° C and drawn to φ2 mm (area reduction: about 55%). Later, it was cooled to room temperature and cold drawn to φ1.5 mm. First, the results of warm drawing are shown in Table 2, and the results of temperature-controlled drawing are shown in Table 3.
本発明例No.1〜28,47〜74と比較例No.29〜46,75〜92は、各特性に及ぼす素材の化学組成の影響を調査したもので、比較例(比較鋼)と比較して本発明例(本発明鋼)の全てにおいて、引張強さが2000N/mm2以上,剛性率が70GPa以上であり、強度および剛性率に優れていた。 Invention Example No. 1-28, 47-74 and Comparative Example No. Nos. 29 to 46 and 75 to 92 were obtained by investigating the influence of the chemical composition of the material on each property, and in all of the inventive examples (invented steels) compared with the comparative examples (compared steels), the tensile strength. Was 2000 N / mm 2 or more and the rigidity was 70 GPa or more, and the strength and rigidity were excellent.
次に請求項1の温間伸線条件の影響について述べる。 Next, the influence of the warm drawing condition of claim 1 will be described.
ここで用いる供試材は、本発明鋼Aを用い、前記工程による溶体化処理後の線材をφ3.0mmまで1次の伸線加工を施し、続いてAr雰囲気で溶体化処理を施した。その後、φ1.5mmまで種々の条件で温間伸線加工(2次伸線加工)を施した。表4にその鋼線製品の特性を示す。 The test material used here was the steel A of the present invention, and the wire after the solution treatment in the above-described step was subjected to primary wire drawing to φ3.0 mm, followed by solution treatment in an Ar atmosphere. Then, warm wire drawing (secondary wire drawing) was performed under various conditions up to φ1.5 mm. Table 4 shows the characteristics of the steel wire product.
本発明例No.93〜98と比較例No.99〜102は、各特性に及ぼす温間伸線条件の影響を調査したもので、比較例と比較して本発明例全てにおいて、引張強さが2000N/mm2以上,剛性率が70GPa以上であり、強度および剛性率に優れていた。 Invention Example No. 93-98 and Comparative Example No. Nos. 99 to 102 are the results of investigating the influence of the warm drawing condition on each property. In all the inventive examples, the tensile strength is 2000 N / mm 2 or more and the rigidity is 70 GPa or more in comparison with the comparative examples. It was excellent in strength and rigidity.
次に請求項2の温度制御伸線条件の影響、すなわち、伸線前段の温間伸線と伸線後段の冷間伸線条件の影響について述べる。 Next, the influence of the temperature-controlled drawing condition of claim 2, that is, the influence of the warm drawing condition before the drawing and the cold drawing condition after the drawing will be described.
ここで用いる供試材は、本発明鋼A,Iを用い、前記工程による溶体化処理後の線材をφ3.0mmまで1次の伸線加工を施し、続いてAr雰囲気で溶体化処理を施して、その後、前段と後段の伸線加工に分けて種々の条件にてφ1.5mmまで温度制御伸線(2次伸線)を施した。表5にその鋼線製品の特性を示す。 The test materials used here are steels A and I of the present invention, and the wire material after the solution treatment in the above process is subjected to primary wire drawing to φ3.0 mm, followed by solution treatment in an Ar atmosphere. After that, temperature-controlled wire drawing (secondary wire drawing) was performed to φ1.5 mm under various conditions by dividing the wire drawing into the former stage and the latter stage. Table 5 shows the characteristics of the steel wire product.
本発明例No.103〜107と比較例No.108〜114は、各特性に及ぼす前段の温間伸線と後段の冷間伸線条件の影響を調査したもので、比較例と比較して本発明例全てにおいて、引張強さが2000N/mm2以上,剛性率が70GPa以上であり、強度および剛性率に優れていた。 Invention Example No. 103-107 and Comparative Example No. Nos. 108 to 114 were obtained by investigating the influence of the warm drawing condition of the former stage and the cold drawing condition of the latter stage on each property, and the tensile strength was 2000 N / mm in all the inventive examples as compared with the comparative example. It was 2 or more and the rigidity was 70 GPa or more, and it was excellent in strength and rigidity.
次に請求項3,4の伸線加工後に時効処理を施した時の実施例について述べる。 Next, an embodiment when the aging treatment is performed after the wire drawing processing of claims 3 and 4 will be described.
表6に時効処理により範囲を拡大した場合の供試材の化学組成を示す。これらの供試材は、前述と同じ方法でφ3.0mmまで鋼線に製造し、続いてAr雰囲気で溶体化処理を施して、その後、φ1.5mmまで2次伸線加工を施した。ここで、2次伸線加工は、伸線前段は150℃に加熱してφ2mm(減面率;約55%)まで伸線加工した後に常温まで冷却してφ1.5mmまで冷間で伸線加工を施した(温度制御伸線)。その後、100〜660℃の温度範囲で低温時効処理を施した。表7にその後の鋼線の製品特性を示す。 Table 6 shows the chemical composition of the test material when the range was expanded by aging treatment. These test materials were manufactured into a steel wire up to φ3.0 mm by the same method as described above, followed by solution treatment in an Ar atmosphere, and then subjected to secondary wire drawing to φ1.5 mm. Here, the secondary wire drawing is performed by heating to 150 ° C. before wire drawing, drawing to φ2 mm (area reduction rate: about 55%), cooling to room temperature, and cold drawing to φ1.5 mm. Processed (temperature controlled wire drawing). Thereafter, a low temperature aging treatment was performed in a temperature range of 100 to 660 ° C. Table 7 shows the product characteristics of the subsequent steel wires.
本発明例No.115〜120と比較例No.121〜126は、各特性に及ぼす
時効処理条件の影響を調査したもので、比較例と比較して本発明例全てにおいて、引張強さが2000N/mm2以上,剛性率が70GPa以上であり、強度および剛性率に優れていた。また、伸線加工後に低温時効処理を施すことで、供試材の化学組成(Mn,Ni,N)の範囲が広がることがわかる。
Invention Example No. 115-120 and Comparative Example No. Nos. 121 to 126 are investigations of the influence of aging treatment conditions on the respective properties. In all of the inventive examples as compared with the comparative examples, the tensile strength is 2000 N / mm 2 or more and the rigidity is 70 GPa or more. Excellent strength and rigidity. Moreover, it turns out that the range of the chemical composition (Mn, Ni, N) of a test material spreads by performing a low temperature aging treatment after a wire drawing process.
本発明の剛性率に優れる高強度ステンレス鋼線およびその製造方法によれば、オーステナイト系ステンレス鋼線の基本成分の規制に加え、伸線加工条件を限定して、オースフォームの強靱化の効果を効率的に使うことで、延靱性と剛性率を著しく向上させた高強度ステンレス鋼線を安定して得ることができる。 According to the high-strength stainless steel wire having excellent rigidity and the manufacturing method thereof according to the present invention, in addition to the restriction of the basic components of the austenitic stainless steel wire, the drawing process conditions are limited, and the effect of toughening ausfoam is obtained. By using it efficiently, a high-strength stainless steel wire with significantly improved ductility and rigidity can be obtained stably.
Claims (10)
Md30=551−462(C+N)−9.2Si−8.1Mn
−29(Ni+Cu)−13.7Cr−18.5Mo ・・・・・・・(1) In mass%, C: 0.03-0.14%, Si: 0.1-4.0%, Mn: 0.1-5.0%, Ni: 2.0-8.0%, Cr: 13.0 to 19.0%, N: 0.005 to 0.21%, the balance is Fe and inevitable components, and the value of Md30 represented by the formula (1) is 25 to 150 (C) High-strength stainless steel with excellent rigidity characterized by heating a wire or steel wire to a warm range of 70 to 400 ° C. and subjecting the wire to a total area reduction ratio of 40 to 95% Manufacturing method of steel wire.
Md30 = 551-462 (C + N) -9.2Si-8.1Mn
-29 (Ni + Cu) -13.7Cr-18.5Mo (1)
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JP6259579B2 (en) * | 2012-03-29 | 2018-01-10 | 新日鐵住金ステンレス株式会社 | High-strength stainless steel wire, high-strength spring, and method of manufacturing the same |
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JP6858931B2 (en) | 2018-06-11 | 2021-04-14 | 日鉄ステンレス株式会社 | Stainless steel wire and its manufacturing method, and spring parts |
KR102169457B1 (en) * | 2018-12-18 | 2020-10-23 | 주식회사 포스코 | High-strength stainless steel |
CN111441001A (en) * | 2020-05-08 | 2020-07-24 | 徐州优尚精密机械制造有限公司 | Low-temperature-resistant functional stainless steel casting and manufacturing method thereof |
JP2022045018A (en) * | 2020-09-08 | 2022-03-18 | マニー株式会社 | Austenite stainless steel-made wire drawing material, medical appliance formed from wire drawing material and wire drawing material processing method |
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JPH0681033A (en) * | 1990-08-30 | 1994-03-22 | Ugine Savoie | Method for producing product very high in breaking load from unstable austenitic stainless steel and product obtained by said method |
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