JPS6357744A - Austenitic stainless steel wire rod combining high strength with high toughness - Google Patents
Austenitic stainless steel wire rod combining high strength with high toughnessInfo
- Publication number
- JPS6357744A JPS6357744A JP19951786A JP19951786A JPS6357744A JP S6357744 A JPS6357744 A JP S6357744A JP 19951786 A JP19951786 A JP 19951786A JP 19951786 A JP19951786 A JP 19951786A JP S6357744 A JPS6357744 A JP S6357744A
- Authority
- JP
- Japan
- Prior art keywords
- stainless steel
- toughness
- austenitic stainless
- steel wire
- strength
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Granted
Links
- 229910000963 austenitic stainless steel Inorganic materials 0.000 title claims abstract description 22
- 229910000831 Steel Inorganic materials 0.000 claims abstract description 33
- 239000010959 steel Substances 0.000 claims abstract description 33
- 239000000203 mixture Substances 0.000 claims abstract description 10
- 229910052698 phosphorus Inorganic materials 0.000 claims abstract description 5
- 229910052717 sulfur Inorganic materials 0.000 claims abstract description 4
- 239000012535 impurity Substances 0.000 claims abstract 2
- 229910052799 carbon Inorganic materials 0.000 abstract description 10
- 229910052757 nitrogen Inorganic materials 0.000 abstract description 9
- 229910052710 silicon Inorganic materials 0.000 abstract description 6
- 229910001220 stainless steel Inorganic materials 0.000 abstract description 6
- 239000010935 stainless steel Substances 0.000 abstract description 5
- PNEYBMLMFCGWSK-UHFFFAOYSA-N aluminium oxide Inorganic materials [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 abstract description 3
- 229910052759 nickel Inorganic materials 0.000 abstract description 3
- 229910052593 corundum Inorganic materials 0.000 abstract description 2
- 229910001845 yogo sapphire Inorganic materials 0.000 abstract description 2
- VYPSYNLAJGMNEJ-UHFFFAOYSA-N Silicium dioxide Chemical compound O=[Si]=O VYPSYNLAJGMNEJ-UHFFFAOYSA-N 0.000 abstract 2
- 230000001105 regulatory effect Effects 0.000 abstract 2
- 229910052681 coesite Inorganic materials 0.000 abstract 1
- 229910052906 cristobalite Inorganic materials 0.000 abstract 1
- VASIZKWUTCETSD-UHFFFAOYSA-N manganese(II) oxide Inorganic materials [Mn]=O VASIZKWUTCETSD-UHFFFAOYSA-N 0.000 abstract 1
- 239000000377 silicon dioxide Substances 0.000 abstract 1
- 235000012239 silicon dioxide Nutrition 0.000 abstract 1
- 229910052682 stishovite Inorganic materials 0.000 abstract 1
- 229910052905 tridymite Inorganic materials 0.000 abstract 1
- 229910001566 austenite Inorganic materials 0.000 description 13
- 238000005452 bending Methods 0.000 description 10
- 238000005260 corrosion Methods 0.000 description 9
- 230000007797 corrosion Effects 0.000 description 8
- 238000012545 processing Methods 0.000 description 8
- 239000006104 solid solution Substances 0.000 description 8
- 230000000694 effects Effects 0.000 description 6
- 229910000734 martensite Inorganic materials 0.000 description 4
- 239000000463 material Substances 0.000 description 4
- 238000005491 wire drawing Methods 0.000 description 4
- 229910000975 Carbon steel Inorganic materials 0.000 description 3
- 239000010962 carbon steel Substances 0.000 description 3
- 238000000034 method Methods 0.000 description 3
- BYFGZMCJNACEKR-UHFFFAOYSA-N aluminium(i) oxide Chemical compound [Al]O[Al] BYFGZMCJNACEKR-UHFFFAOYSA-N 0.000 description 2
- 230000000052 comparative effect Effects 0.000 description 2
- 238000005336 cracking Methods 0.000 description 2
- 238000010586 diagram Methods 0.000 description 2
- 229910000967 As alloy Inorganic materials 0.000 description 1
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 1
- 238000002441 X-ray diffraction Methods 0.000 description 1
- 238000004458 analytical method Methods 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 239000003795 chemical substances by application Substances 0.000 description 1
- 230000002301 combined effect Effects 0.000 description 1
- 239000012141 concentrate Substances 0.000 description 1
- 229910052802 copper Inorganic materials 0.000 description 1
- 239000010949 copper Substances 0.000 description 1
- 238000006073 displacement reaction Methods 0.000 description 1
- 238000011156 evaluation Methods 0.000 description 1
- 229910052739 hydrogen Inorganic materials 0.000 description 1
- 238000007654 immersion Methods 0.000 description 1
- 238000004519 manufacturing process Methods 0.000 description 1
- 238000005259 measurement Methods 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 229910052760 oxygen Inorganic materials 0.000 description 1
- 238000010587 phase diagram Methods 0.000 description 1
- 238000007747 plating Methods 0.000 description 1
- 239000002994 raw material Substances 0.000 description 1
- 238000011160 research Methods 0.000 description 1
- 229920006395 saturated elastomer Polymers 0.000 description 1
- 230000006641 stabilisation Effects 0.000 description 1
- 238000011105 stabilization Methods 0.000 description 1
- 238000012360 testing method Methods 0.000 description 1
- 229910000859 α-Fe Inorganic materials 0.000 description 1
Landscapes
- Heat Treatment Of Steel (AREA)
- Heat Treatment Of Strip Materials And Filament Materials (AREA)
Abstract
Description
【発明の詳細な説明】
［産業上の利用分野コ
本発明は高強度、高靭性オーステナイト系ステンレス鋼
線材に関し、ざらに詳しくは事務機器、電気機器、精密
機器、建築物、自動車等の産業分野において、耐蝕性の
要求される部品、例えば、耐蝕性ばね、ロッド、シャフ
ト、ピン類に使用されるオーステナイト系ステンレス鋼
線材に関する。[Detailed Description of the Invention] [Industrial Application Fields] The present invention relates to high strength and high toughness austenitic stainless steel wire rods, and more specifically, to industrial fields such as office equipment, electrical equipment, precision equipment, buildings, and automobiles. The present invention relates to an austenitic stainless steel wire used in parts requiring corrosion resistance, such as corrosion-resistant springs, rods, shafts, and pins.
［従来技術］
従来、高強度オーステナイト系ステンレス鋼としては、
５ＵＳ３０４が主として使用されてきているが、強度が
炭素鋼ピアノ線と比較すると、かなり低い。即ち、ＪＩ
Ｓにおいても、
炭素鋼ピアノ線
Ｊ Ｉ Ｓ（Ｇ ３５２２）ＳＷＰ−Ｂ ２φ、引張強
さ２０５〜２２５Ｋｇｆ／ｍｍ２、
オーステナイト系ステンレス鋼
ＪＩＳ（Ｇ４３１４）ＳＵＳ３０４−ＷＰＢ２φ、引張
強さ１７０〜１９５ Ｋｇｆ／關２と規定化されており
、ステンレス鋼の引張強さは低い水準にあり、そのため
、高強度が必要な部品製造においは、ステンレス鋼の形
状寸法の大型化あるいはピアノ線に防蝕メッキを施す等
の繁雑な加工工程を必要としているのが現状である。[Prior art] Conventionally, high-strength austenitic stainless steel
5US304 has been mainly used, but its strength is considerably lower than that of carbon steel piano wire. That is, J.I.
Also in S, carbon steel piano wire JIS (G 3522) SWP-B 2φ, tensile strength 205-225 Kgf/mm2, austenitic stainless steel JIS (G4314) SUS304-WPB 2φ, tensile strength 170-195 Kgf/mm2 2, and the tensile strength of stainless steel is at a low level. Therefore, when manufacturing parts that require high strength, it is necessary to increase the size of the stainless steel or apply anti-corrosion plating to the piano wire. The current situation is that it requires complicated processing steps.
また、成型加工」この開運としては、ばね、ロッド類の
端部は構造物に取り付けるための曲げ加工を施すことが
多いが、高強度綱は一般に靭性が低いために加工割れの
トラブルを発生ずることである。In addition, the ends of springs and rods are often bent to attach them to structures, but high-strength steels generally have low toughness, which causes problems such as processing cracks. That's true.
［発明が解決しようとする問題点］
本発明は上記に説明したように、従来におけろオーステ
ナイト系ステンレスλ４の問題点や加工上の問題点に鑑
み、本発明者が鋭意研究を行い、検討を重ねた結果、産
業構造が重厚長大型から軽薄短小型へ展開している中で
、オーステナイト系ステンレス鋼線材に高性能（高強度
）を付与し、かつ、成型性の良好な高強度、高靭性オー
ステナイト系ステンレス鋼線材を開発したのである。[Problems to be Solved by the Invention] As explained above, the present invention has been made in view of the problems and processing problems of conventional austenitic stainless steel λ4. As a result of repeated efforts, as industrial structures have evolved from heavy, long and large to light, thin, short and small, we have been able to provide high performance (high strength) to austenitic stainless steel wire rods, as well as high strength and high strength with good formability. They developed a tough austenitic stainless steel wire.
Ｅ問題点を解決するだめの手段〕
本発明にかかる高強度、高靭性オーステナイト系ステン
レス鋼線材の特徴とするところは、Ｃ０．０４〜０．１
０ｗｔ％、Ｓ ｉ １．５０〜２．５０ｗｔ％、〜ｌｎ
ＯＪＯ〜２．００ｗｔ％、Ｐ ６０．０４５ｗｔ％、
Ｓ ≦０，０３０ｗｔ％、Ｎｉ ６．００〜１０．５０
ｖｔ％、Ｃｒ １７．００〜２０．００ｗｔ％、ＡＩ
≦ ０．００７ｗｔ％、Ｎ ０．１５〜０．２５ｗ
ｔ％
を含有し、残’Ｆｌ’ｒ Ｆ ｅおよび不純物からなり
、鋼中の酸化物系非金属介在物の組成範囲が、Ｓ ｉｏ
ｔ ２０〜ｌｏｏｗｔ％、ＭｎＯＯ〜５０ｗｔ％、Ａ
ｌｘ ０３０〜３０ｗｔ％
であることにある。[Means to Solve Problem E] The high strength and high toughness austenitic stainless steel wire according to the present invention is characterized by a C0.04 to 0.1
0wt%, Si 1.50-2.50wt%, ~ln
OJO~2.00wt%, P 60.045wt%,
S≦0,030wt%, Ni 6.00-10.50
vt%, Cr 17.00-20.00wt%, AI
≦ 0.007wt%, N 0.15~0.25w
The composition range of oxide-based nonmetallic inclusions in steel is S io
t 20~lowt%, MnOO~50wt%, A
lx 030 to 30 wt%.
本発明に係る高強度、高靭性オーステナイト系ステンレ
ス鋼線材が高性能となるのは次の理由による。The high-strength, high-toughness austenitic stainless steel wire according to the present invention has high performance for the following reasons.
（１）高強度を付与する手段
合金成分として、Ｃ，Ｓｉ、Ｈの最適量を曵合金有させ
、これらの成分の固溶硬化作用により高強度が得られる
のである。そして、Ｃ，Ｎは鋼中に浸入型に固溶硬化し
、Ｓｉは鋼中に置換型に固溶硬化するが、従来Ｓｉの固
溶硬化については積極的に考慮されていなかった。本発
明に係る高強度、高靭性オーステナイト系ステンレス鋼
においてはＳｉをＣＳＮと複合含有させることいより、
顕著に強度が上昇することを見出だし、Ｃ，Ｓｉ、Ｎを
積極的に含有させて高強度を得るものである。(1) Means for imparting high strength By incorporating optimum amounts of C, Si, and H as alloy components, high strength can be obtained through the solid solution hardening effect of these components. C and N undergo solid solution hardening in steel in an immersive manner, and Si undergoes solid solution hardening in steel in a displacement manner, but solid solution hardening of Si has not been actively considered in the past. In the high-strength, high-toughness austenitic stainless steel according to the present invention, by containing Si in combination with CSN,
It was discovered that the strength significantly increased, and high strength was obtained by actively incorporating C, Si, and N.
（２）高靭性を付与する手段
オーステナイト系ステンレス鋼線材の靭性低下の原因は
二つあり、一つは鋼中の酸化物系介在物であり、他の一
つは伸線加工中に生成する加工誘起マルテンサイトであ
る。(2) Means for imparting high toughness There are two causes for the decrease in toughness of austenitic stainless steel wire. One is oxide inclusions in the steel, and the other is generated during wire drawing. It is deformation-induced martensite.
鋼中の酸化物系金属介在物の組成、形態について、即ち
、従来ステンレス鋼では、酸化物の主成分はＡｌ２Ｏ＊
系であって、このＡｌ２Ｏ３は硬質で塑性変形しない角
状のＣ型介在物となり、この角状介在物は曲げ加工時に
応ツノ集中を受は易く、加工割れ発生の起点として作用
ずろので、本発明に係る高強度、高靭性オーステナイト
系ステンレス鋼線材においては、Ｓｉ含有量と介在物組
成、形態について研究の結果、Ｓｉ含有量を増加させ、
Ａ１含有量を低減することによって、鋼中酸化物の主成
分を８１０．系に変換し、形態としては延伸型（Ａ２型
）に変えろことができることを知見し、そして、この延
伸型介在物は１１１１げ加工時の集中応力を緩和し靭性
値の向上に寄与ケるのである。Regarding the composition and morphology of oxide-based metal inclusions in steel, that is, in conventional stainless steel, the main component of oxides is Al2O*
This Al2O3 forms angular C-shaped inclusions that are hard and do not deform plastically, and these angular inclusions easily receive stress concentration during bending and act as starting points for the occurrence of processing cracks. In the high-strength, high-toughness austenitic stainless steel wire according to the invention, as a result of research on Si content, inclusion composition, and morphology, the Si content is increased,
By reducing the A1 content, the main component of oxides in the steel can be reduced to 810. It was found that the shape could be changed to a stretched type (A2 type), and that these stretched inclusions alleviated the concentrated stress during 1111 processing and contributed to improving the toughness value. be.
次に、伸線加工中に生成する加工誘起マルテンサイトに
ついて、従来ステンレス鋼においては多量に生成するこ
とは避けられず、マルテンサイト相は硬質で脆い組織で
あるので、曲げ加工時の靭性低下、割れ発生の原因とな
っていた。しかして、本発明に係る高強度、高靭性オー
ステナイト系ステンレス鋼線材においては、Ｃ，Ｎの含
有量を増加することによって、伸線加工後においてもマ
ルテンサイト相の生成を少なく抑制できる事、即ち、安
定したオーステナイト相を得ることを認めろ七共にオー
ステナイト相の安定化により曲げ靭性値が向上すること
がわかった。Next, regarding strain-induced martensite that is generated during wire drawing, it is unavoidable that it is generated in large amounts in conventional stainless steel, and since the martensite phase is a hard and brittle structure, it causes a decrease in toughness during bending. This caused cracks to occur. Therefore, in the high-strength, high-toughness austenitic stainless steel wire according to the present invention, by increasing the content of C and N, the formation of martensitic phase can be suppressed to a small extent even after wire drawing. It was found that the stabilization of the austenite phase improves the bending toughness value.
本発明に係る高強度、高靭性に優れたオーステナイト系
ステンレス鋼線材の含有成分および成分割合について説
明する。The components and component ratios of the austenitic stainless steel wire having excellent high strength and high toughness according to the present invention will be explained.
Ｃは鋼に浸入型に固溶し強度を上昇すると共に、オース
テナイト相を安定させるのに必要な元素であり、含有量
が０．０４ｗｔ％未満ではこの効果は少なく、また、０
．１ｈｔ％を越えて過剰に含有されると炭化物を生成し
、耐蝕性を劣化させる。よって、Ｃ含有量は０．０４〜
０．１０ｗｔ％とする。C is an element necessary to form a solid solution in steel and increase its strength, as well as to stabilize the austenite phase. If the content is less than 0.04 wt%, this effect will be small, and
．． If the content exceeds 1 ht%, carbide is generated and corrosion resistance is deteriorated. Therefore, the C content is 0.04~
The content shall be 0.10 wt%.
Ｓｉは製銅脱酸剤として含有されるが、さらに、積極的
に、鋼中に置換型に固溶硬化させると共に、鋼中の酸化
物の主成分をＳｉｎ、にするためには、１．５０ｗｔ％
以上含有させる必要があり、また、２．５０ｗｔ％を越
えて含有されると、熱間加工性を悪くする。よって、Ｓ
ｉ含有量は１．５０〜２，５０ｗｔ％とする。Si is contained as a copper deoxidizing agent, but in order to actively solid-solution harden the steel in a substitutional manner and to make Si the main component of oxides in the steel, 1. 50wt%
It is necessary to contain more than 2.50 wt%, and if the content exceeds 2.50 wt%, hot workability will be deteriorated. Therefore, S
The i content is 1.50 to 2,50 wt%.
Ｍｎは鋼中ＳとＭｒ＋Ｓを生成し、熱間加工性改善のた
めには０４０ｗｔ％の含有は必要であり、また、含有量
が２．００ｗｔ％を越えて含有されると耐蝕性を低下さ
せる。よって、Ｍｎ含有ｍは０．３０〜２．００ｖｔ％
とする。Mn forms S and Mr+S in steel, and inclusion of 0.40 wt% is necessary to improve hot workability, and if the content exceeds 2.00 wt%, corrosion resistance will be reduced. . Therefore, Mn content m is 0.30 to 2.00vt%
shall be.
Ｐは靭性および耐蝕性の面からは低い程好ましいもので
あるが、不可避的に混入してくるので、含有量は５０．
０４５ｗ１％とする。From the viewpoint of toughness and corrosion resistance, the lower the P content, the more preferable it is, but since it is inevitably mixed in, the content should be 50.
045w1%.
ＳもＰと同様に靭性および耐蝕性のめんから低い程好ま
しいが、不可避的に混入してくるので含有ｍは０．０３
０ｗｔ％とする。Similarly to P, S is preferably as low as possible due to its toughness and corrosion resistance, but since S is unavoidably mixed, the content m is 0.03
It is set to 0wt%.
Ｎｉは鋼のオーステナイト域を拡大して常温においてオ
ーステナイト組織とするのに必要であり、含有量が６．
００ｗｔ％未満ではこの効果はなく、また、１０．５０
ｗｔ％を越えて含有されると上記の効果は飽和してしま
い高価であることから無駄である。Ni is necessary to expand the austenite region of steel to form an austenite structure at room temperature, and the content is 6.
This effect is absent at less than 00 wt%, and 10.50 wt%
If the content exceeds wt%, the above effect will be saturated and it will be expensive, which is wasteful.
よって、Ｎｉ含有量は６．００〜１０．５ｈｔ％とする
。Therefore, the Ni content is set to 6.00 to 10.5 ht%.
Ｃｒは安定した耐蝕性を得るために、１７．００ｗｔ％
の含有は必要であり、また、２０．００ｗｔ％を越えて
含有されるとフェライト相を生成しオーステナイト相と
２相組織となって熱間加工性を低下させる。Cr is 17.00wt% to obtain stable corrosion resistance.
In addition, if the content exceeds 20.00 wt%, a ferrite phase is formed and a two-phase structure with an austenite phase is formed, resulting in a decrease in hot workability.
よって、Ｃｒ含有量は１７．００〜２０．００ｗｔ％と
する。Therefore, the Cr content is set to 17.00 to 20.00 wt%.
ＡＩは鋼中に硬質のＡｌｔｏｓ酸化物を生成し、靭性を
劣化させる有害成分であるが、製ｊ１４原料から不可避
的に残留するので、含有量は６０．００７ｗ１％とする
。AI is a harmful component that produces hard Altos oxide in steel and deteriorates toughness, but since it inevitably remains from the J14 raw material, the content is set to 60.007w1%.
ＮはＣと同様に浸入型に固溶して強度を上昇させると共
に、オーステナイト相を安定さける元素であり、伸線加
工後のオーステナイト相の占有率を９０％以上とするた
めには、含有量は０．１５ｗｔ％以上は必要で、また、
０．２５ｗｔ％越えて多く含有されると応力腐食割れを
促進する。よって、Ｎ含有量は０．１５〜０．２５ｗｔ
％とする。Like C, N is an element that increases the strength by solid solution in an immersion type and also stabilizes the austenite phase.In order to make the occupancy of the austenite phase after wire drawing 90% or more, the content must be increased. is required to be at least 0.15wt%, and
If the content exceeds 0.25 wt%, stress corrosion cracking will be promoted. Therefore, the N content is 0.15 to 0.25wt
%.
「実 施 例Ｊ
本発明に係る高強度、高靭性オーステナイト系ステンレ
ス鋼線材について実施例を説明する。``Example J'' An example of a high-strength, high-toughness austenitic stainless steel wire according to the present invention will be described.
実施例
第１表は、本発明に係る高強度、高靭性オーステナイト
系ステンレス鋼線材（本発明鋼ということがある。）は
番号１．２．３、比較鋼は番号４．５．６、従来鋼は７
の含有成分および含有割合を示す。In Table 1 of Examples, the high-strength, high-toughness austenitic stainless steel wire rod according to the present invention (sometimes referred to as the present invention steel) is numbered 1.2.3, the comparative steel is numbered 4.5.6, and the conventional steel wire is numbered 1.2.3. steel is 7
Indicates the contained components and content ratios.
第１図は、Ｎ含有量と２ｍｍφ線の品質特性を示す。FIG. 1 shows the N content and quality characteristics of the 2 mmφ wire.
先ず、引張強さについてみると、Ｎ含有量が増すと増加
し、０．１５ｗｔ％以上含有させると引張強さは炭素鋼
ピアノ線のＪＩＳ規格以上の２１０Ｋｇ／＋ｎａ＋２以
上の高強度が得られることがわかる。これはＮが同時に
含有されているＣ、Ｓｉと複合効果を発揮し強度向上に
寄与していることによる。First, looking at the tensile strength, it increases as the N content increases, and when the content is 0.15 wt% or more, a high tensile strength of 210 kg/+na+2 or more, which is higher than the JIS standard for carbon steel piano wire, can be obtained. I understand. This is because N exhibits a combined effect with C and Si, which are also contained, contributing to an improvement in strength.
これに対し、比較ｗ４４．５．６では２１０Ｋｇ／ｍｍ
”以上の高強度には達していない。この理由は、比較ｊ
！ｊ１４．５．６に含有されているＮ、Ｃ。On the other hand, in comparison w44.5.6, it is 210Kg/mm.
The reason for this is that compared to
! N and C contained in j14.5.6.
Ｓｔの含有量が本発明鋼に比べて低いため充分な固溶硬
化が得られないからである。This is because sufficient solid solution hardening cannot be obtained because the St content is lower than that of the steel of the present invention.
次に、オーステナイト相の安定度を見ると、Ｎ含有量が
０．１５ｗｔ％以上である本発明鋼はオーステナイト相
占有率率９０％以上を示し、組織が安定していることが
わかる。これに対し、比較鋼４．５はＮまたはＣの含有
量が低いためオーステナイト相占有率が低いことがわか
る。この場合は、Ｘ線回折法による測定結果である。Next, looking at the stability of the austenite phase, it can be seen that the steel of the present invention with an N content of 0.15 wt% or more exhibits an austenite phase occupancy rate of 90% or more, and has a stable structure. On the other hand, it can be seen that Comparative Steel 4.5 has a low austenite phase occupancy due to a low content of N or C. In this case, the measurement results are based on the X-ray diffraction method.
さらに、２ｍｍφ線の靭性評価法として曲げ試験を実施
したが、曲げ回数は本発明鋼ではオーステナイト相の安
定度に対応して１６回以上の高い回数が得られ、靭性の
高い実用材料として適している。この場合の曲げは曲げ
ツール５ｍｍＲでの９０°曲げ回数を示す。Furthermore, a bending test was conducted as a toughness evaluation method for the 2mmφ wire, and the steel of the present invention had a high number of bending times of 16 or more, which corresponds to the stability of the austenite phase, making it suitable as a practical material with high toughness. There is. The bending in this case indicates the number of times of 90° bending with a bending tool of 5 mmR.
第２図は鋼中酸化物の組成分析結果をＳ ｉＯを−Ｍｎ
Ｏ−ＡＩ２０３三元状＠図にプロットしたものである。Figure 2 shows the compositional analysis results of oxides in steel.
It is plotted on the O-AI203 ternary diagram.
従来鋼の酸化物組成はＡＩｔｏ、、ＭｎＯを主成分とし
て、その成分はＳ ｉｏ ｔ ０〜２０ｗｔ％、ＭｎＯ
Ｏ〜１０ｈｔ％、Ａｌ２Ｏ２０〜１００ｗｔ％の領域に
分布することがわかる（第２図ではへて示しである。）
。The oxide composition of conventional steel is mainly composed of AIto, MnO, and its components are Siot 0 to 20 wt%, MnO
It can be seen that it is distributed in the range of O to 10 ht% and Al2O20 to 100 wt% (Fig. 2 shows the range).
.
これに対して、本発明鋼はＳｌを積極的に１，５０ｗｔ
％以上多量に含有させていることから、酸化物組成は従
来鋼と異なり、成分は５ｉＯｖを主成分として、Ｓ ｉ
ｏ ｔ ２０〜１００ｗｔ％、ＭｎＯＯ〜５０ｗｔ％、
ＡＬｏ、０〜３Ｋｔ％の領域に分布していることがわか
る（第２図では斜線の○でしめしである。）。On the other hand, the steel of the present invention actively contains 1,50wt of Sl.
% or more, the oxide composition is different from conventional steel, with the main component being 5iOv, Si
ot 20-100wt%, MnOO-50wt%,
It can be seen that ALo is distributed in the range of 0 to 3 Kt% (indicated by a diagonal circle in FIG. 2).
従来鋼に存在するＡｌｔＯｉ−ＭｎＯ系の酸化物は熱間
加工工程で延伸せず、鋼材においてＣ型角状の介在物と
して残存し、曲げ加工時に応力集中し割れの起点となっ
て鋼材の靭性を劣化させる。これに対して、本発明鋼に
認められるＳｉｎ、系の酸化物は変形能を有し延伸ずろ
ので、屑材加工時に応力集中を緩和することにより靭性
の向上に寄与するのである。The AltOi-MnO-based oxides present in conventional steels are not stretched during the hot working process and remain in the steel material as C-shaped angular inclusions, which concentrate stress during bending and serve as starting points for cracks, reducing the toughness of the steel material. deteriorate. On the other hand, since the Sin-based oxides found in the steel of the present invention have deformability and stretch, they contribute to improving toughness by alleviating stress concentration during processing of scrap materials.
［発明の効果］
以上説明しｊこように、本発明に係る高強度、高靭性オ
ーステナイト系ステンレス舖線材は上記の構成であるか
ら、引張強さ２１０ Ｋｇｆ／ｍｍ”以上を存すると共
に曲げ靭性にら浸れており、さらに、加工靭性に優れ、
加工工程において割れ、折損等のトラブルを生じろこと
か無いという効果を有する。[Effects of the Invention] As explained above, since the high-strength, high-toughness austenitic stainless steel wire rod according to the present invention has the above-mentioned configuration, it has a tensile strength of 210 Kgf/mm or more and has excellent bending toughness. In addition, it has excellent processing toughness,
It has the effect that troubles such as cracking and breakage do not occur during the processing process.
第１図はＮ含有量と引張強さ、オーステナイト占有率お
よび曲げ回数との関係を示す図、第２図はＳｉＯｘ−Ｍ
ｎ０−ＡＩ２０ｚの状態図における本発明に係る高強度
、高靭性オーステナイト系ステンレス鋼線材と従来鋼の
酸化物組成分領域を示す図である。
！！−２図
Ｓ、Ｏ工Figure 1 shows the relationship between N content, tensile strength, austenite occupancy, and number of bends, and Figure 2 shows the relationship between the N content, tensile strength, austenite occupancy, and number of bends.
FIG. 2 is a diagram showing the oxide composition regions of the high-strength, high-toughness austenitic stainless steel wire according to the present invention and conventional steel in the phase diagram of n0-AI20z. ! ! -2 Figure S, O engineering
Claims (1)
ｗｔ％、Ｍｎ０．３０〜２．００ｗｔ％、Ｐ≦０．０４
５ｗｔ％、Ｓ≦０．０３０ｗｔ％、Ｎｉ６．００〜１０
．５０ｗｔ％、Ｃｒ１７．００〜２０．００ｗｔ％、Ａ
ｌ≦０．００７ｗｔ％、Ｎ０．１５〜０．２５ｗｔ％ を含有し、残部Ｆｅおよび不純物からなり、鋼中の酸化
物系非金属介在物の組成範囲が、 ＳｉＯ＿２２０〜１００ｗｔ％、ＭｎＯ０〜５０ｗｔ％
、Ａｌ＿２Ｏ＿３０〜３０ｗｔ％ であることを特徴とする高強度、高靭性オーステナイト
系ステンレス鋼線材。[Claims] C0.04-0.10wt%, Si1.50-2.50
wt%, Mn0.30-2.00wt%, P≦0.04
5wt%, S≦0.030wt%, Ni6.00-10
．． 50wt%, Cr17.00-20.00wt%, A
l≦0.007wt%, N0.15-0.25wt%, the balance consists of Fe and impurities, and the composition range of oxide-based nonmetallic inclusions in the steel is SiO_220-100wt%, MnO0-50wt%.
, Al_2O_30 to 30 wt%. A high-strength, high-toughness austenitic stainless steel wire rod.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP19951786A JPS6357744A (en) | 1986-08-26 | 1986-08-26 | Austenitic stainless steel wire rod combining high strength with high toughness |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP19951786A JPS6357744A (en) | 1986-08-26 | 1986-08-26 | Austenitic stainless steel wire rod combining high strength with high toughness |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS6357744A true JPS6357744A (en) | 1988-03-12 |
| JPH0241579B2 JPH0241579B2 (en) | 1990-09-18 |
Family
ID=16409139
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP19951786A Granted JPS6357744A (en) | 1986-08-26 | 1986-08-26 | Austenitic stainless steel wire rod combining high strength with high toughness |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS6357744A (en) |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH01298115A (en) * | 1988-05-26 | 1989-12-01 | Sumitomo Electric Ind Ltd | Production of high strength stainless steel wire |
| JP2002146483A (en) * | 2000-11-09 | 2002-05-22 | Nippon Steel Corp | High strength austenitic stainless steel wire |
Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS57177955A (en) * | 1981-03-24 | 1982-11-01 | Nippon Steel Corp | Stainless steel with enhanced passivating capacity |
-
1986
- 1986-08-26 JP JP19951786A patent/JPS6357744A/en active Granted
Patent Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS57177955A (en) * | 1981-03-24 | 1982-11-01 | Nippon Steel Corp | Stainless steel with enhanced passivating capacity |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH01298115A (en) * | 1988-05-26 | 1989-12-01 | Sumitomo Electric Ind Ltd | Production of high strength stainless steel wire |
| JP2002146483A (en) * | 2000-11-09 | 2002-05-22 | Nippon Steel Corp | High strength austenitic stainless steel wire |
| JP4489928B2 (en) * | 2000-11-09 | 2010-06-23 | 新日鐵住金ステンレス株式会社 | High strength austenitic stainless steel wire |
Also Published As
| Publication number | Publication date |
|---|---|
| JPH0241579B2 (en) | 1990-09-18 |
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