JPH02305940A - Two-phase stainless steel for building material - Google Patents
Two-phase stainless steel for building materialInfo
- Publication number
- JPH02305940A JPH02305940A JP12666589A JP12666589A JPH02305940A JP H02305940 A JPH02305940 A JP H02305940A JP 12666589 A JP12666589 A JP 12666589A JP 12666589 A JP12666589 A JP 12666589A JP H02305940 A JPH02305940 A JP H02305940A
- Authority
- JP
- Japan
- Prior art keywords
- stainless steel
- steel
- phase
- relaxation
- phase stainless
- 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
- 239000004566 building material Substances 0.000 title claims abstract description 8
- 229910001220 stainless steel Inorganic materials 0.000 title abstract description 19
- 239000010935 stainless steel Substances 0.000 title abstract description 9
- 229910052757 nitrogen Inorganic materials 0.000 claims abstract description 10
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 9
- 229910052802 copper Inorganic materials 0.000 claims abstract description 7
- 229910052710 silicon Inorganic materials 0.000 claims abstract description 7
- 239000012535 impurity Substances 0.000 claims abstract description 5
- 229910052719 titanium Inorganic materials 0.000 claims abstract description 5
- 229910052720 vanadium Inorganic materials 0.000 claims abstract description 5
- 229910001566 austenite Inorganic materials 0.000 claims description 17
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 8
- 229910001039 duplex stainless steel Inorganic materials 0.000 claims description 8
- 229910052742 iron Inorganic materials 0.000 claims description 4
- 229910052748 manganese Inorganic materials 0.000 abstract description 7
- 229910052759 nickel Inorganic materials 0.000 abstract description 7
- 229910052758 niobium Inorganic materials 0.000 abstract description 3
- 229910052799 carbon Inorganic materials 0.000 abstract 2
- 229910000831 Steel Inorganic materials 0.000 description 27
- 239000010959 steel Substances 0.000 description 27
- 230000007797 corrosion Effects 0.000 description 11
- 238000005260 corrosion Methods 0.000 description 11
- 239000011651 chromium Substances 0.000 description 8
- 239000004035 construction material Substances 0.000 description 6
- 238000001816 cooling Methods 0.000 description 4
- 230000000694 effects Effects 0.000 description 4
- 229910000859 α-Fe Inorganic materials 0.000 description 4
- 229910000975 Carbon steel Inorganic materials 0.000 description 3
- 229910045601 alloy Inorganic materials 0.000 description 3
- 239000000956 alloy Substances 0.000 description 3
- 239000010962 carbon steel Substances 0.000 description 3
- 238000005336 cracking Methods 0.000 description 3
- 230000007423 decrease Effects 0.000 description 3
- 238000010438 heat treatment Methods 0.000 description 3
- 238000002844 melting Methods 0.000 description 3
- 230000008018 melting Effects 0.000 description 3
- 239000000203 mixture Substances 0.000 description 3
- 238000005275 alloying Methods 0.000 description 2
- 230000006698 induction Effects 0.000 description 2
- 239000000463 material Substances 0.000 description 2
- 230000003014 reinforcing effect Effects 0.000 description 2
- 238000005728 strengthening Methods 0.000 description 2
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 2
- 206010023204 Joint dislocation Diseases 0.000 description 1
- 229910018487 Ni—Cr Inorganic materials 0.000 description 1
- 229910000963 austenitic stainless steel Inorganic materials 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 239000003795 chemical substances by application Substances 0.000 description 1
- UFGZSIPAQKLCGR-UHFFFAOYSA-N chromium carbide Chemical compound [Cr]#C[Cr]C#[Cr] UFGZSIPAQKLCGR-UHFFFAOYSA-N 0.000 description 1
- 230000000052 comparative effect Effects 0.000 description 1
- 238000009749 continuous casting Methods 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 238000005261 decarburization Methods 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- PCHJSUWPFVWCPO-UHFFFAOYSA-N gold Chemical compound [Au] PCHJSUWPFVWCPO-UHFFFAOYSA-N 0.000 description 1
- 229910052737 gold Inorganic materials 0.000 description 1
- 239000010931 gold Substances 0.000 description 1
- 238000005098 hot rolling Methods 0.000 description 1
- 238000011835 investigation Methods 0.000 description 1
- 229910000734 martensite Inorganic materials 0.000 description 1
- 229910001105 martensitic stainless steel Inorganic materials 0.000 description 1
- 238000000034 method Methods 0.000 description 1
- 229910052750 molybdenum Inorganic materials 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 239000000047 product Substances 0.000 description 1
- 238000007670 refining Methods 0.000 description 1
- 238000005096 rolling process Methods 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
- 229910003470 tongbaite Inorganic materials 0.000 description 1
Landscapes
- Heat Treatment Of Steel (AREA)
Abstract
Description
【発明の詳細な説明】
（産業上の利用分野）
本発明は建築建材用として使用される強度が高くレラク
セーション（ステンレス鋼にある応力を与え、その時に
生ずる歪が一定に保たれるような条件で放置すると、時
間の経過とともに初めに与えた応力が次第に減少する現
象で、その減少の小さい程すぐれた性質と評価されてい
る。）の小さい安価なオーステナイト・フェライト系二
相ステンレス鋼に関する。[Detailed Description of the Invention] (Industrial Application Field) The present invention is a high-strength relaxation steel used as a construction material. This is a phenomenon in which the initially applied stress gradually decreases over time when left under such conditions, and the smaller the decrease, the better the properties. .
（従来の技術）
従来建築建材用には安価で強度が高い理由で、例えばＪ
ＩＳに規定されたＳＭ鋼のような普通炭素鋼が使用され
てきたが、普通炭素鋼は耐食性をもたないために無塗装
で使用される場合はもちろん、たとえ塗装して使用され
る場合でも腐食による消耗は避けられず建築構造物とし
ての寿命が短くなる原因になり、また発錆により美観も
損なわれるなどの欠点をもっている。このような現状に
おいて、将来は耐久性や美観の点でこれらの晋通炭素鋼
にかわりステンレス鋼の使用が期待されている。しかし
ながら、従来のステンレス鋼をこのような用途に使用す
る場合幾つかの問題がある。(Conventional technology) Conventionally, J-
Ordinary carbon steel such as SM steel specified by IS has been used, but ordinary carbon steel does not have corrosion resistance, so it cannot be used unpainted or even if it is painted. Wear and tear due to corrosion is unavoidable and causes a shortened lifespan as a building structure, and it also has drawbacks such as rusting that impairs its aesthetic appearance. Under these current circumstances, it is expected that stainless steel will be used in place of Jintong carbon steel in the future due to its durability and aesthetics. However, there are several problems when using conventional stainless steel in such applications.
たとえば、Ｓ Ｕ Ｓ ３０４やＳ Ｕ Ｓ ３１６な
どに代表されるオーステナイト系ステンレス鋼は、溶接
性が優れているためステンレス鋼の中でも最も適してい
るように思われるが、一般に強度（耐力）かや−低いた
めレラクセーションが大きい。その上、多量のＮｉを含
有するために高価である。また、Ｓ Ｕ Ｓ ４１０で
代表されるマルテンサイト系ステンレス鋼やＳ Ｕ Ｓ
４３０に代表されるフェライト系ステンレス鋼はレラ
クセーションも小さく、オーステナイト系ステンレス鋼
に比べれば安価であるが、溶接性が劣る問題点がある。For example, austenitic stainless steels such as SUS 304 and SUS 316 seem to be the most suitable among stainless steels because of their excellent weldability, but they generally have low strength (yield strength) and -It is low and provides great relaxation. Moreover, it is expensive because it contains a large amount of Ni. In addition, martensitic stainless steel represented by SUS 410 and SUS
Ferritic stainless steels such as 430 have low relaxation and are cheaper than austenitic stainless steels, but they have the problem of poor weldability.
またこれらのオーステナイト系と、マルテンサイト系や
フェライト系ステンレス鋼の中間的な特性をもつ鋼とし
て５ＵＳ３２９Ｊｌに代表されるオーステナイト・フェ
ライト系ステンレス鋼があるが、この鋼はオーステナイ
ト系と同等程度に溶接性が優れ、オーステナイト系ステ
ンレス鋼の欠点である粒界腐食や応力腐食割れに対する
抵抗性も強いことから化学機器などに多く使用されてい
る。In addition, there is austenitic/ferritic stainless steel represented by 5US329Jl, which has properties intermediate between these austenitic stainless steels and martensitic and ferritic stainless steels, but this steel has weldability comparable to that of austenitic stainless steels. It is widely used in chemical equipment because of its excellent corrosion resistance and strong resistance to intergranular corrosion and stress corrosion cracking, which are disadvantages of austenitic stainless steels.
（発明が解決しようとする課題）
本発明は上述したような溶接性に優れた二相ステンレス
鋼に着目し、その成分を特定することによってレラクセ
ーションが著しく小さく且つ建築建材用に一般的に要求
されるＪＩＳ ＳＭ ４１．５０と同等あるいはそれ以
上の機械的性質すなわち、室温での耐力（ｐｓ）が４０
ｋｇ ｆ ／ ｍａｔ以上、引張り強さくＴＳ）が６０
）ｃｇ ｆ ／−以上、伸び（ＩＪ））が２０％以上、
０℃におけるシャルピー吸収エネルギー（ｖＥｏ）が２
．８ｋｇ−ｍ以上であって、室温におけるレラクセーシ
ョンが小さいという特性を有する建築建材用二相ステン
レス鋼を提供することを目的とするものである。(Problems to be Solved by the Invention) The present invention focuses on the above-mentioned duplex stainless steel with excellent weldability, and by specifying its components, it has extremely low relaxation and is generally suitable for construction materials. Mechanical properties equivalent to or higher than the required JIS SM 41.50, i.e. proof stress (ps) at room temperature of 40
kg f/mat or more, tensile strength (TS) is 60
) cg f /- or more, elongation (IJ)) is 20% or more,
Charpy absorbed energy (vEo) at 0°C is 2
．． The object of the present invention is to provide a duplex stainless steel for building materials having a weight of 8 kg-m or more and low relaxation at room temperature.
（課題を解決するための手段）
本発明は、
（ｔ） ｃ ： ｏ、ｔｏ％以下、Ｓ ｉ：０．１
〜３．０％、Ｍｎ：０．１〜５．０％、Ｃｒ：１９．０
〜２６．０％、Ｎ Ｉ：１．０〜６．０％、Ｎ ： ０
．０５〜０．４０％を含有し、残りが鉄および不可避的
不純物から成り、かつオーステナイト相面積率が２０〜
８０％であることを特徴とする建築建材用二相ステンレ
ス鋼、
（２） Ｃ： ０．１０％以下、Ｓ ｉ：０．１〜
ａ、ｏ％、Ｍｎ：０．１〜５．０％、Ｃｒ：１９．ｏ
〜２８．０％、Ｎｉ：１．０〜８．０％、Ｎ ： ０．
０５〜０，４０％、およびＮｂ：０．０１〜２．０％、
Ｔ ｉ：０．ｏｌ〜２．０％、Ｖ ： ０．０１〜２．
０％、Ｃｕ：０．１〜３．０％のうち１種あるいは２種
以上を含有し、残りが鉄および不可避的不純物から成り
、かつオーステナイト相面積率が２０〜８０％であるこ
とを特徴とする建築建材用二相ステンレス鋼、
である。(Means for Solving the Problems) The present invention provides the following: (t) c: o, to% or less, Si: 0.1
~3.0%, Mn: 0.1~5.0%, Cr: 19.0
~26.0%, NI: 1.0~6.0%, N: 0
．． 05-0.40%, the remainder consists of iron and unavoidable impurities, and the austenite phase area ratio is 20-0.40%.
duplex stainless steel for architectural construction materials, characterized in that: (2) C: 0.10% or less; Si: 0.1~
a, o%, Mn: 0.1-5.0%, Cr: 19. o
~28.0%, Ni: 1.0~8.0%, N: 0.
05-0.40%, and Nb: 0.01-2.0%,
Ti:0. ol~2.0%, V: 0.01~2.
0%, Cu: 0.1 to 3.0%, the remainder consists of iron and inevitable impurities, and the austenite phase area ratio is 20 to 80%. Duplex stainless steel for architectural construction materials.
以下に、本発明鋼について詳細に説明する。Below, the steel of the present invention will be explained in detail.
５ＵＳ３２９Ｊ１で代表される現行二相ステンレス鋼は
孔食や応力腐食割れに対する抵抗性を高めるために高価
な合金成分のＭｏを通常数％含有している。しかし、建
築材料として使用される場合には、ＣΩ−環境は少いの
で孔食や応力腐食割れに起因する損傷が起こることは少
なく、必然的に適正な鋼成分も変わってくる。このよう
な前提のもとに、各種機械的性質に与える二相ステンレ
ス鋼の相バランス支配元素としてＣｒ。Current duplex stainless steels, such as 5US329J1, usually contain several percent of Mo, an expensive alloying component, to increase resistance to pitting corrosion and stress corrosion cracking. However, when used as a building material, the CΩ environment is low, so damage due to pitting corrosion or stress corrosion cracking is less likely to occur, and the appropriate steel composition will inevitably change. Based on this premise, Cr is used as the element controlling the phase balance of duplex stainless steel that affects various mechanical properties.
Ｎｉ 、Ｍｎ 、Ｎ、Ｓｌなど、および強化元素トして
Ｎｂ、Ｔｉ 、Ｖ、Ｃｕなどの各種元素の影響を調べた
結果、Ｃ： ０．１０％以下、Ｓ ｉ：ｏ、１〜３．０
％、Ｍｎ：０．１〜５．０％、Ｃｒ：１９．ｏ 〜２Ｅ
ｆ、Ｏ％、Ｎｉ：１．０〜６．０％、Ｎ ： ０．０５
〜０．４０％を金白゛しあるいはサラｌ： Ｎ ｂ：０
．ｏｌ〜２．０％、Ｔ ｉ：０．０１〜２．０９６、■
＝０．０１〜２．０％、Ｃｕ：０．１〜３．０％の１種
または２種以上を含む鋼により目標の特性を満足できる
ことがわかった。As a result of investigating the effects of various elements such as Ni, Mn, N, Sl, and reinforcing elements such as Nb, Ti, V, and Cu, the results showed that C: 0.10% or less, Si: o, 1 to 3. 0
%, Mn: 0.1-5.0%, Cr: 19. o ~2E
f, O%, Ni: 1.0-6.0%, N: 0.05
~0.40% gold or white: N b: 0
．． ol ~ 2.0%, Ti: 0.01 ~ 2.096, ■
It has been found that the target properties can be satisfied with steel containing one or more of Cu=0.01 to 2.0% and Cu: 0.1 to 3.0%.
このように鋼成分を限定した理由は次のとおりである。The reason for limiting the steel components in this way is as follows.
Ｃ：Ｃｒを多量に含むステンレス鋼においてＣの含有は
クロム炭化物を生成して粒界に析出し、耐食性を低下さ
せるため、その含有量を０，１５％以下にした。C: In stainless steel containing a large amount of Cr, the content of C forms chromium carbide and precipitates at grain boundaries, reducing corrosion resistance, so the content was set to 0.15% or less.
Ｓｌ ：フエライト形成元素で二相鋼におけるフェライ
ト相の量をコントロールする。そしてこの元素の添加に
より有効に強度を上げることができる。Sl: A ferrite-forming element that controls the amount of ferrite phase in duplex steel. By adding this element, the strength can be effectively increased.
この強化のためには少なくとも（１，１％添加しなけれ
ばその効果を発揮することができず、その含有量の増加
に強度を増大せしめるが過剰の添加は熱間加工性妻低下
させるため３％以下とする必要がある。For this strengthening, the effect cannot be exhibited unless at least (1.1%) is added, and as the content increases, the strength increases, but excessive addition reduces hot workability. % or less.
Ｍｎ：Ｎｉのかわりに使用する安価で有力なオーステナ
イト形成元素で、二相鋼におけるオーステナイト相の量
をコントロールし、レラクセーションを安定して小さく
する作用する役目をもつ。Mn: An inexpensive and effective austenite-forming element used in place of Ni, which controls the amount of austenite phase in duplex steel and has the role of stably reducing relaxation.
そしてこの成分の添加により有効に強度を増大する。こ
の強化のためには少なくとも０．１％添加しなければそ
の効果を発揮することができない。また、Ｍｎの過剰添
加はオーステナイト相を増やしレラクセーションを窩め
るため、５％以下でなければならない。The addition of this component effectively increases the strength. For this strengthening, the effect cannot be exhibited unless at least 0.1% is added. Further, excessive addition of Mn increases the austenite phase and impairs relaxation, so the amount must be 5% or less.
Ｃ「：耐食性保有のためと、フェライト形成元素である
ためフェライト相の星のコントロールのために必要な元
素で、そのためには少なくとも１９．０％以上含有しな
ければならない。しかし、いたずらに多量の含をは合金
コストが高くなるだけである。したがって、その上限を
２Ｂ％にした。C: It is an element necessary for maintaining corrosion resistance and controlling stars in the ferrite phase because it is a ferrite-forming element.For this purpose, it must be contained at least 19.0%.However, an unnecessarily large amount of Containing only increases the alloy cost.Therefore, the upper limit was set at 2B%.
Ｎ１ ：二相鋼におけるオーステナイト柑形成に必要な
元素で、そのためには少なくとも１％含有しなければな
らない。しかし多量の添加は相バランスとしてオーステ
ナイト相の割合を増やし、レラクセーションを高め、そ
の上合金コストが高くなるのでその量は６％以下でなけ
ればならない。N1: An element necessary for the formation of austenite in duplex steel, and for this purpose it must be contained at least 1%. However, addition of a large amount increases the proportion of austenite phase as a phase balance, increases relaxation, and also increases alloy cost, so the amount must be 6% or less.
Ｎ：Ｎｉと同じように二相鋼においてオーステナイト相
を増やし強度を上げる元素で、そのためには少なくとも
０．０５％含有しなければならない。N: Like Ni, it is an element that increases the austenite phase in duplex steel to increase its strength, and for this purpose it must be contained at least 0.05%.
しかし多量の添加は相バランスとしてオーステナイト相
の割合を増やし、さらに気泡発生による内部欠陥生成の
原因になるため、０，４０％以下でなければならない。However, addition of a large amount increases the proportion of the austenite phase as a phase balance and causes internal defects due to the generation of bubbles, so the content must be 0.40% or less.
これらの合金元素の他に、強化元素として、Ｎ ｂ：０
．０１〜２．０ ％、Ｔ ｊ：Ｏ，Ｏ１〜２．０９６、
Ｖ：０．０１〜２．０％およびＣｕ：Ｏ，１〜３．０％
のうち１種または２８ｉ以上を含有させることができる
。すなわち、これらの元素を０．０１％以上含有するこ
とにより結晶粒が微細になり強度とくに降伏強度を上昇
せしめる。しかし多量の添加は靭性を著しく低下せしめ
る結果となるため、２．０％以下でなければならない。In addition to these alloying elements, as a reinforcing element, Nb:0
．． 01-2.0%, Tj:O, O1-2.096,
V: 0.01-2.0% and Cu: O, 1-3.0%
One type or 28i or more of them can be contained. That is, by containing these elements in an amount of 0.01% or more, the crystal grains become finer and the strength, particularly the yield strength, is increased. However, addition of a large amount will result in a significant decrease in toughness, so the content must be 2.0% or less.
また、本発明鋼は、このような合金成分範囲を満足する
と同時に、製品として、必ずオーステナイト相とフェラ
イト相との二相から成らなければならず、それらの存在
比率は面積百分率で２０〜８０％好ましくは３０〜７０
％である。第１図に本発明鋼すなわち建築建材用鋼の特
性の一つとして要求されるレラクセーションと、オース
テナイト相面積百分率（％）との関係を示したが、これ
によりオーステナイト相が８０％を超えるとレラクセー
ションが急激に大きくなることがわかる。また２０％を
切ると、後述する実施例からもわかるように目標とする
機械的性質が得られない。本発明はこのような比率を満
足することによって、建築建材用として必要な諸性質を
一層改善する。In addition, the steel of the present invention must satisfy the alloy composition range as described above, and at the same time, the product must be composed of two phases, an austenite phase and a ferrite phase, and their abundance ratio is 20 to 80% in area percentage. Preferably 30-70
%. Figure 1 shows the relationship between relaxation, which is required as one of the characteristics of the steel of the present invention, that is, steel for building materials, and the area percentage (%) of the austenite phase. It can be seen that the relaxation increases rapidly. Moreover, if it is less than 20%, the target mechanical properties cannot be obtained, as can be seen from the examples described later. By satisfying such ratios, the present invention further improves various properties necessary for use in architectural construction materials.
以下に実施例により説明する。Examples will be explained below.
実施例 １
Ｃ： ０．０１〜０，０３％、Ｓ ｉ ：０．４〜０．
７９ｇ、Ｍｎ：１．７〜１．８％、Ｃｒ：１７．ｏ 〜
２３．０％、Ｎｉ：６％以下、ＭＯ・３％以下、Ｎ ：
０．１２〜０．１７％を含む２０ｋｇの鋼塊を真空誘
導溶解炉により溶製し、これらの鋼塊を厚さ１３順に熱
間圧延した後、１１００℃で３０分間保定したのち水焼
入れよりなる溶体化処理を行い、材質調査を行った。Ｃ
ｒ及びＮｉの含有量とγ相の面積百分率、ＰＳ、ＴＳ、
Ｅｊ７． ｖＥｏの値との関係を第２図（Ａ）〜（Ｅ
）に示す。この結果がら、Ｃｒ量が１９％に満たない場
合にはγ相面債百分率は２０％に満たずまたα′フマル
ンサイトが生成してＰＳやＴＳが著しくａＪ＜ＩＪＩは
２０％に満たない。Example 1 C: 0.01-0.03%, Si: 0.4-0.
79g, Mn: 1.7-1.8%, Cr: 17. o ~
23.0%, Ni: 6% or less, MO・3% or less, N:
20 kg of steel ingots containing 0.12 to 0.17% were melted in a vacuum induction melting furnace, hot rolled in order of 13 thicknesses, held at 1100°C for 30 minutes, and then water quenched. We conducted a solution treatment and investigated the material properties. C
r and Ni content and area percentage of γ phase, PS, TS,
Ej7. The relationship with the value of vEo is shown in Figure 2 (A) to (E
). From this result, when the Cr content is less than 19%, the γ-phase bond percentage is less than 20%, and α' fumarunsite is generated, resulting in significant PS and TS, and aJ<IJI is less than 20%. .
すなわち、本発明の目標特性を満足するためにはＣ「は
１９．０％以上でなければならない。Ｎｉについては、
１％に満たない場合にはα＃目だけより成り、したがっ
てｖＥｏは極めて低い。６％を超えた場合にはγ相が多
くなり、レラクセーションを小さくできない。このよう
な理由から、Ｎｉ量−は１，０〜６．０％の範囲でなけ
ればならない。That is, in order to satisfy the target characteristics of the present invention, C must be 19.0% or more. Regarding Ni,
If it is less than 1%, it consists only of the α# order, and therefore vEo is extremely low. If it exceeds 6%, the amount of γ phase increases and relaxation cannot be reduced. For these reasons, the Ni content must be in the range of 1.0 to 6.0%.
実施例 ２
真空誘導溶解炉ニヨリ、Ｃ： ０．０１〜０．（１８％
、Ｓ ｉ：０．５〜２．７％、Ｍｎ：０．８〜４．［ｉ
％、Ｎｉ：１．９〜４．５％、Ｃｒ：１９〜２８％、Ｎ
： ０．０９〜０．３２％、その他に選択元素として
、Ｎｂ：０．０５〜０．１２％、Ｔｉ：０．ＬＯ〜０．
２０％、Ｖ ： ０．０５〜０．［％およびＣｕ：Ｃ１
，５〜１．５％を含む第１表に示す、ような組成の鋼塊
を作製した。これらの鋼塊を厚さ２５＋ｎｕ＋に熱間圧
延した後、１０５０〜１１５０℃で溶体化熱処理を行っ
た。これらの鋼板の引張特性値、衝撃特性値およびレラ
クセーション率を第２表に示した。レラクセーション率
は初期応力−耐力Ｘ０．８、試験温度−２０℃±０．５
℃、試験時間−１０ｈｒにて、自動制御槓桿型しラクセ
ーション試験機により、月Ｓ Ｚ ２２７Ｂに準拠して
ｎ１定した。Example 2 Vacuum induction melting furnace Niyori, C: 0.01-0. (18%
, Si: 0.5-2.7%, Mn: 0.8-4. [i
%, Ni: 1.9-4.5%, Cr: 19-28%, N
: 0.09 to 0.32%, and other selected elements include Nb: 0.05 to 0.12%, Ti: 0. LO~0.
20%, V: 0.05-0. [% and Cu:C1
, 5 to 1.5%, steel ingots having the composition shown in Table 1 were prepared. After hot rolling these steel ingots to a thickness of 25+nu+, they were subjected to solution heat treatment at 1050 to 1150°C. Table 2 shows the tensile property values, impact property values, and relaxation rates of these steel plates. Relaxation rate is initial stress - proof stress x0.8, test temperature -20℃±0.5
℃, test time -10 hr, n1 was determined in accordance with Moon S Z 227B using an automatically controlled ram type luxation tester.
第１表および第２表において、鋼Ｎ０９１〜Ｉ８の鋼は
本発明鋼であるが、Ｎｏ、 １９はＳ Ｕ Ｓ ３０４
、Ｎｏ、２０はＳ Ｕ Ｓ ４１０ 、Ｎｏ、２１は
５Ｍ４０の代表例を比較鋼として示している。In Tables 1 and 2, steels No. 091 to I8 are steels of the present invention, but No. 19 is SUS 304.
, No. 20 shows typical examples of SUS 410, and No. 21 shows representative examples of 5M40 as comparison steels.
Ｎ０１１〜１８の本発明鋼はオーステナイト相とフェラ
イト相より成る二相組織てそれらのオーステナイト相の
占める面積百分率は３０〜７０％の範囲に入っていた。The invention steels No. 11 to 18 had a two-phase structure consisting of an austenite phase and a ferrite phase, and the area percentage occupied by the austenite phase was in the range of 30 to 70%.
これらの本発明鋼の機械的性質は目標とするＰＳ４０ｋ
ｇｆ／−以上、ＴＳ８０ｋｇｆ／−以上、Ｅｊ７２０％
以上、ｖＥｏ ２．８ｋｇ ｆ −ｍ以上を十分に満足
し、特にＰＳとＴＳの強度は比較鋼の５ＵＳ３０４，５
ＵＳ４１０および５Ｍ４０よりはるかに高い。また本発
明鋼の常温におけるレラクセーションはＳＭ鋼に近くき
わめて小さく建築構造物用として適している。The mechanical properties of these inventive steels meet the target PS40k.
gf/- or more, TS80kgf/- or more, Ej720%
As mentioned above, vEo of 2.8 kg f-m or more is fully satisfied, and especially the strength of PS and TS is higher than that of comparative steel 5US304,5.
Much higher than US410 and 5M40. Further, the relaxation of the steel of the present invention at room temperature is close to that of SM steel and is extremely small, making it suitable for use in building structures.
なお、本発明鋼は、ステンレス鋼の溶製法としてよく知
られた、転炉や電気炉と真空脱炭精錬などとの組合せで
溶製され、連続鋳造、または造塊と分塊圧延によりスラ
ブにされる。このスラブは一旦室温にまで冷却されるか
あるいは必ずしも室温にまで冷却されることなく加熱炉
に装入して加熱した後１２００〜６００℃の温度範囲で
厚板に圧延される。圧延後の冷却は自然放冷でもよいし
水冷などの強制冷却でもよい。続いて必要に応じ９５０
〜１２００℃の温度範囲で溶体化熱処理が行われる。The steel of the present invention is melted by a combination of a converter or electric furnace and vacuum decarburization refining, which is a well-known melting method for stainless steel, and is made into a slab by continuous casting or ingot making and blooming. be done. This slab is once cooled to room temperature, or is charged into a heating furnace without necessarily being cooled to room temperature, heated, and then rolled into a thick plate at a temperature in the range of 1200 to 600°C. Cooling after rolling may be done by natural cooling or by forced cooling such as water cooling. Then 950 if necessary
Solution heat treatment is performed at a temperature range of ~1200°C.
（発明の効果）
以上説明したように、本発明は成分を特定することによ
り、５Ｍ４１．５０クラスと同等或はそれ以上の特性を
もち、しかもレラクセーションが小さいことから建築建
材用に適した二相ステンレス鋼を安価に製造できるので
、工業的価値は極めて大きい。(Effects of the Invention) As explained above, by specifying the components, the present invention has properties equivalent to or better than those of the 5M41.50 class, and has low relaxation, making it suitable for construction materials. Since duplex stainless steel can be manufactured at low cost, its industrial value is extremely large.
第１図はオーステナイト柑面積率（％）とレラクセーシ
ョン率の関係、第２図（Ａ）〜（Ｅ）は実施例１におけ
る材質調査結果を示すもので、（Ａ）は耐力（ＳＰ）、
（Ｂ）は引張り強さくＴＳ）、 （Ｃ）は破断伸び（Ｅ
ｌ） ’）、 （Ｄ）はシャルピー吸収エネルギー（ｖ
Ｅｏ）、（Ｅ）はオーステナイト相面積分率（Ｆγ）を
Ｎｉ−Ｃｒ含有量との関係で示した。
復代理人 弁理士 田村弘明
オーステナイト相面積分率（％）
第２図
（Ｃ）
ＩＶ／ （％）
第２図Figure 1 shows the relationship between the austenite area ratio (%) and relaxation rate, and Figures 2 (A) to (E) show the results of material investigation in Example 1. (A) shows the proof stress (SP). ,
(B) is the tensile strength (TS), (C) is the elongation at break (E
l) '), (D) is the Charpy absorbed energy (v
Eo) and (E) show the austenite phase area fraction (Fγ) in relation to the Ni-Cr content. Sub-agent Patent Attorney Hiroaki Tamura Austenite phase area fraction (%) Figure 2 (C) IV/ (%) Figure 2
Claims (2)
Ｍｎ：０．１〜５．０％、Ｃｒ：１９．０〜２６．０％
、Ｎｉ：１．０〜６．０％、Ｎ：０．０５〜０．４０％
を含有し、残りが鉄および不可避的不純物から成り、か
つオーステナイト相面積率が２０〜８０％であることを
特徴とする建築建材用二相ステンレス鋼。(1) C: 0.10% or less, Si: 0.1 to 3.0%,
Mn: 0.1-5.0%, Cr: 19.0-26.0%
, Ni: 1.0-6.0%, N: 0.05-0.40%
1. A duplex stainless steel for building materials, characterized in that the remainder consists of iron and unavoidable impurities, and has an austenite phase area ratio of 20 to 80%.
Ｍｎ：０．１〜５．０％、Ｃｒ：１９．０〜２６．０％
、Ｎｉ：１．０〜６．０％、Ｎ：０．０５〜０．４０％
、およびＮｂ：０．０１〜２．０％、Ｔｉ：０．０１〜
２．０％、Ｖ：０．０１〜２．０％、Ｃｕ：０．１〜３
．０％のうち１種あるいは２種以上を含有し、残りが鉄
および不可避的不純物から成り、かつオーステナイト相
面積率が２０〜８０％であることを特徴とする建築建材
用二相ステンレス鋼。(2) C: 0.10% or less, Si: 0.1 to 3.0%,
Mn: 0.1-5.0%, Cr: 19.0-26.0%
, Ni: 1.0-6.0%, N: 0.05-0.40%
, and Nb: 0.01~2.0%, Ti: 0.01~
2.0%, V: 0.01-2.0%, Cu: 0.1-3
．． A duplex stainless steel for building materials, characterized in that it contains one or more of 0%, the remainder consists of iron and unavoidable impurities, and has an austenite phase area ratio of 20 to 80%.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP1126665A JPH0768603B2 (en) | 1989-05-22 | 1989-05-22 | Duplex stainless steel for building materials |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP1126665A JPH0768603B2 (en) | 1989-05-22 | 1989-05-22 | Duplex stainless steel for building materials |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH02305940A true JPH02305940A (en) | 1990-12-19 |
| JPH0768603B2 JPH0768603B2 (en) | 1995-07-26 |
Family
ID=14940842
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP1126665A Expired - Lifetime JPH0768603B2 (en) | 1989-05-22 | 1989-05-22 | Duplex stainless steel for building materials |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH0768603B2 (en) |
Cited By (19)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH05247594A (en) * | 1992-03-03 | 1993-09-24 | Sumitomo Metal Ind Ltd | Dual phase stainless steel excellent in weatherability |
| EP0750053A1 (en) * | 1994-12-16 | 1996-12-27 | Sumitomo Metal Industries, Ltd. | Duplex stainless steel excellent in corrosion resistance |
| JP2006169622A (en) * | 2004-01-29 | 2006-06-29 | Jfe Steel Kk | Austenitic-ferritic stainless steel with excellent formability |
| JP2006183129A (en) * | 2004-01-29 | 2006-07-13 | Jfe Steel Kk | Austenitic-ferritic stainless steel having excellent formability |
| JP2006233308A (en) * | 2005-02-28 | 2006-09-07 | Jfe Steel Kk | Austenitic-ferritic stainless steel having excellent grain boundary corrosion resistance |
| EP1715073A1 (en) * | 2004-01-29 | 2006-10-25 | JFE Steel Corporation | Austenitic-ferritic stainless steel |
| KR100834595B1 (en) * | 2001-10-30 | 2008-06-02 | 에이티아이 프로퍼티즈, 인코퍼레이티드 | Duplex Stainless Steel |
| EP2025770A1 (en) * | 2007-08-09 | 2009-02-18 | Nisshin Steel Co., Ltd. | Ni-reduced austenite stainless steel |
| JP2009035782A (en) * | 2007-08-02 | 2009-02-19 | Nippon Steel & Sumikin Stainless Steel Corp | Ferritic-austenitic stainless steel with excellent corrosion resistance and workability, and its manufacturing method |
| JP2009052115A (en) * | 2007-08-29 | 2009-03-12 | Nippon Steel & Sumikin Stainless Steel Corp | Ferritic-austenitic stainless steel sheet having excellent formability, and method for producing the same |
| WO2009048137A1 (en) | 2007-10-10 | 2009-04-16 | Nippon Steel & Sumikin Stainless Steel Corporation | Duplex stainless steel wire material, steel wire, bolt, and method for production of the bolt |
| EP2093303A1 (en) * | 2008-09-04 | 2009-08-26 | Scanpump AB | Duplex Cast Steel |
| US8313691B2 (en) | 2007-11-29 | 2012-11-20 | Ati Properties, Inc. | Lean austenitic stainless steel |
| US8337748B2 (en) | 2007-12-20 | 2012-12-25 | Ati Properties, Inc. | Lean austenitic stainless steel containing stabilizing elements |
| US8337749B2 (en) | 2007-12-20 | 2012-12-25 | Ati Properties, Inc. | Lean austenitic stainless steel |
| WO2013113718A1 (en) * | 2012-02-03 | 2013-08-08 | Klaus Kuhn Edelstahlgiesserei Gmbh | Duplex steel with improved notch-impact strength and machinability |
| US8877121B2 (en) | 2007-12-20 | 2014-11-04 | Ati Properties, Inc. | Corrosion resistant lean austenitic stainless steel |
| EP2172574A4 (en) * | 2007-08-02 | 2017-06-07 | Nippon Steel & Sumikin Stainless Steel Corporation | Ferritic-austenitic stainless steel excellent in corrosion resistance and workability and process for manufacturing the same |
| JP2021025082A (en) * | 2019-08-02 | 2021-02-22 | 新報国製鉄株式会社 | Two-phase stainless steel casting |
Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS6156267A (en) * | 1984-03-30 | 1986-03-20 | サントレ−ド リミテイド | Ferrite-austenite copper alloy having high corrosion resistance and good weldability |
-
1989
- 1989-05-22 JP JP1126665A patent/JPH0768603B2/en not_active Expired - Lifetime
Patent Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS6156267A (en) * | 1984-03-30 | 1986-03-20 | サントレ−ド リミテイド | Ferrite-austenite copper alloy having high corrosion resistance and good weldability |
Cited By (32)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH05247594A (en) * | 1992-03-03 | 1993-09-24 | Sumitomo Metal Ind Ltd | Dual phase stainless steel excellent in weatherability |
| EP0750053A1 (en) * | 1994-12-16 | 1996-12-27 | Sumitomo Metal Industries, Ltd. | Duplex stainless steel excellent in corrosion resistance |
| EP0750053A4 (en) * | 1994-12-16 | 1998-04-01 | Sumitomo Metal Ind | Duplex stainless steel excellent in corrosion resistance |
| KR100834595B1 (en) * | 2001-10-30 | 2008-06-02 | 에이티아이 프로퍼티즈, 인코퍼레이티드 | Duplex Stainless Steel |
| JP2006169622A (en) * | 2004-01-29 | 2006-06-29 | Jfe Steel Kk | Austenitic-ferritic stainless steel with excellent formability |
| JP2006183129A (en) * | 2004-01-29 | 2006-07-13 | Jfe Steel Kk | Austenitic-ferritic stainless steel having excellent formability |
| EP1715073A1 (en) * | 2004-01-29 | 2006-10-25 | JFE Steel Corporation | Austenitic-ferritic stainless steel |
| EP1715073A4 (en) * | 2004-01-29 | 2007-09-26 | Jfe Steel Corp | Austenitic-ferritic stainless steel |
| US8562758B2 (en) | 2004-01-29 | 2013-10-22 | Jfe Steel Corporation | Austenitic-ferritic stainless steel |
| JP2006233308A (en) * | 2005-02-28 | 2006-09-07 | Jfe Steel Kk | Austenitic-ferritic stainless steel having excellent grain boundary corrosion resistance |
| JP2009035782A (en) * | 2007-08-02 | 2009-02-19 | Nippon Steel & Sumikin Stainless Steel Corp | Ferritic-austenitic stainless steel with excellent corrosion resistance and workability, and its manufacturing method |
| EP3434802A1 (en) * | 2007-08-02 | 2019-01-30 | Nippon Steel & Sumikin Stainless Steel Corporation | Ferritic-austenitic stainless steel excellent in corrosion resistance and workability and method of production of same |
| EP2172574A4 (en) * | 2007-08-02 | 2017-06-07 | Nippon Steel & Sumikin Stainless Steel Corporation | Ferritic-austenitic stainless steel excellent in corrosion resistance and workability and process for manufacturing the same |
| EP2025770A1 (en) * | 2007-08-09 | 2009-02-18 | Nisshin Steel Co., Ltd. | Ni-reduced austenite stainless steel |
| JP2009052115A (en) * | 2007-08-29 | 2009-03-12 | Nippon Steel & Sumikin Stainless Steel Corp | Ferritic-austenitic stainless steel sheet having excellent formability, and method for producing the same |
| WO2009048137A1 (en) | 2007-10-10 | 2009-04-16 | Nippon Steel & Sumikin Stainless Steel Corporation | Duplex stainless steel wire material, steel wire, bolt, and method for production of the bolt |
| US10370748B2 (en) | 2007-11-29 | 2019-08-06 | Ati Properties Llc | Lean austenitic stainless steel |
| US8313691B2 (en) | 2007-11-29 | 2012-11-20 | Ati Properties, Inc. | Lean austenitic stainless steel |
| US9617628B2 (en) | 2007-11-29 | 2017-04-11 | Ati Properties Llc | Lean austenitic stainless steel |
| US8858872B2 (en) | 2007-11-29 | 2014-10-14 | Ati Properties, Inc. | Lean austenitic stainless steel |
| US8337749B2 (en) | 2007-12-20 | 2012-12-25 | Ati Properties, Inc. | Lean austenitic stainless steel |
| US9121089B2 (en) | 2007-12-20 | 2015-09-01 | Ati Properties, Inc. | Lean austenitic stainless steel |
| US9133538B2 (en) | 2007-12-20 | 2015-09-15 | Ati Properties, Inc. | Lean austenitic stainless steel containing stabilizing elements |
| US8877121B2 (en) | 2007-12-20 | 2014-11-04 | Ati Properties, Inc. | Corrosion resistant lean austenitic stainless steel |
| US9624564B2 (en) | 2007-12-20 | 2017-04-18 | Ati Properties Llc | Corrosion resistant lean austenitic stainless steel |
| US9822435B2 (en) | 2007-12-20 | 2017-11-21 | Ati Properties Llc | Lean austenitic stainless steel |
| US9873932B2 (en) | 2007-12-20 | 2018-01-23 | Ati Properties Llc | Lean austenitic stainless steel containing stabilizing elements |
| US8337748B2 (en) | 2007-12-20 | 2012-12-25 | Ati Properties, Inc. | Lean austenitic stainless steel containing stabilizing elements |
| US10323308B2 (en) | 2007-12-20 | 2019-06-18 | Ati Properties Llc | Corrosion resistant lean austenitic stainless steel |
| EP2093303A1 (en) * | 2008-09-04 | 2009-08-26 | Scanpump AB | Duplex Cast Steel |
| WO2013113718A1 (en) * | 2012-02-03 | 2013-08-08 | Klaus Kuhn Edelstahlgiesserei Gmbh | Duplex steel with improved notch-impact strength and machinability |
| JP2021025082A (en) * | 2019-08-02 | 2021-02-22 | 新報国製鉄株式会社 | Two-phase stainless steel casting |
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|---|---|
| JPH0768603B2 (en) | 1995-07-26 |
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