JP2011184717A - Ferritic stainless free-cutting steel bar wire having excellent forgeability - Google Patents
Ferritic stainless free-cutting steel bar wire having excellent forgeability Download PDFInfo
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- 229910000831 Steel Inorganic materials 0.000 claims abstract description 33
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- 239000002131 composite material Substances 0.000 claims abstract description 16
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- 239000012535 impurity Substances 0.000 claims abstract description 3
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Abstract
Description
本発明は、鍛造性と被削性に優れるフェライト系ステンレス鋼に関するものであり、例えば、これまで切削加工のみで製造している複雑な形状を有した精密部品の製造を、鍛造加工でニアネットシェイプ化を行い、仕上げ加工として切削加工を行うことにより、材料歩留よく加工することが可能なフェライト系ステンレス鋼に関するものである。 The present invention relates to a ferritic stainless steel excellent in forgeability and machinability. For example, the manufacture of precision parts having complicated shapes that have been manufactured only by cutting until now can be performed by forging. The present invention relates to a ferritic stainless steel that can be processed with a high material yield by performing shaping and cutting as finishing.
フェライト系ステンレス鋼は磁性を有し、加工性、耐食性などに優れた性質を有することから、様々な分野において広く使用されている。ネジ、ボルトなどの各種機器部品は一般に鍛造によって成形加工して製造されることが多い。この鍛造による加工方法は能率、歩留が高い利点を有するが、精密な加工精度に劣る。一方、複雑な形状を有する精密部品では、すべて切削加工で製造されている。切削加工による方法では複雑な形状への加工が可能であり、非常に精密な寸法精度を満足することができる利点があるものの、太い線径の材料から加工されるため材料歩留が悪いという欠点がある。 Ferritic stainless steel is widely used in various fields because it has magnetism and has excellent properties such as workability and corrosion resistance. In general, various equipment parts such as screws and bolts are generally manufactured by being formed by forging. This forging processing method has the advantages of high efficiency and yield, but is inferior in precise processing accuracy. On the other hand, all precision parts having complicated shapes are manufactured by cutting. The cutting method allows processing into complex shapes and has the advantage of satisfying very precise dimensional accuracy, but has the disadvantage of poor material yield because it is processed from a material with a large wire diameter. There is.
従来、鍛造加工により製造される部品にはＳＵＳ４３０（１６％Ｃｒ）が、切削加工により製造される部品にはＳＵＳ４３０F（１６％Ｃｒ−０．３％Ｓ）などが用いられてきた。鍛造性に優れたＳＵＳ４３０は被削性が悪く、被削性の優れたＳＵＳ４３０Ｆは鍛造性が悪いという相反する特徴を有している。従って、複雑な形状を有する部品では材料歩留が悪くても被削性の高い鋼を使用し、切削加工にて製造しているのが通常であった。
そこで、冷間加工性と被削性を併せ持つ鋼として、下記特許文献１、２に記載されている鋼が提案されている。
Conventionally, SUS430 (16% Cr) has been used for parts manufactured by forging, and SUS430F (16% Cr-0.3% S) has been used for parts manufactured by cutting. SUS430 having excellent forgeability has a contradictory feature that machinability is poor, and SUS430F having excellent machinability has poor forgeability. Therefore, parts having a complicated shape are usually manufactured by cutting using steel having high machinability even if the material yield is low.
Then, the steel described in the following
特許文献１はＴｉ添加により硫化物を微細分散し冷間鍛造性を損なうことなく、被削性を向上させたことを特徴とする鋼である。しかし、Ｃｒ量が低いことから、十分な耐食性が得られず、現行ステンレス鋼が使用されている環境下においては、発銹の問題が考えられる。
特許文献２に記載された発明は、Ｔｉ、Ｃ、Ｎ、Ｓ量を制御することにより優れた冷鍛性と被削性を併せ持つフェライト系ステンレス鋼である。しかし、Ｔｉ系の介在物は比較的硬質で有り、工具磨耗に悪影響を及ぼすことが考えられるものの、その影響については検討されていなかった。
The invention described in
以上のように、これまで、Ｃａ、Ａｌ、Ｏの成分バランスによりコストアップさせることなく、介在物の形態を制御し、鍛造性と被削性の両特性をバランスよく付与したフェライト系ステンレス快削鋼は提案されていなかった。 As described above, ferritic stainless steel free-cutting that controls the form of inclusions and provides both forgeability and machinability in a balanced manner without increasing costs due to the balance of Ca, Al, and O components. Steel was not proposed.
本発明は、介在物の制御により、鍛造性にすぐれたフェライト系ステンレス快削鋼を提供することで、これまで切削加工のみで行われてきた部品加工の歩留を鍛造加工との組み合わせにより向上させることを課題とする。 The present invention provides ferritic stainless steel free-cutting steel with excellent forgeability by controlling inclusions, thereby improving the yield of parts processing that has been performed only by cutting by combining with forging. Let's make it an issue.
本発明は、前記課題を解決するためになされたもので、酸化物系介在物の組成をコントロールすることにより、酸化物と硫化物の複合介在物を形成、微細分散させることによって、鍛造性を向上させようとした結果、極微量のＡｌ、Ｃａ、Ｏの量、比率を制御することで、鍛造性を劣化させることなく、被削性を確保できることを見出したものである。
すなわち、本発明の要旨とするところは特許請求の範囲の記載した通りの下記内容である。
（１）質量%で、Ｃ≦０．１２０％、Ｓｉ：０．１〜２．０％、Ｍｎ：０．１〜３．０％、Ｐ≦０．０５％、S：０．０１％〜０．２０％、Ｃｒ：１１．０〜３０．０％、Ｎ≦０．２５０％、Ａｌ：０．００２〜０．０１０％、Ｃａ：０．００１〜０．０１０％、Ｏ：０．００１％〜０．０２５％、残部Ｆｅおよび不可避的不純物からなる鋼で、かつ質量比で０．２５≦Ｃａ／Ａｌ≦２．５０および０．１０≦Ｃａ／Ｏ≦０．３０の条件を満たすことにより、低軟化点を有するＣａＯ−ＳｉＯ2−Ａｌ2Ｏ3系の酸化物と（Ｍｎ,Ｃｒ）Ｓの硫化物との複合介在物を形成することを特徴とする鍛造性に優れるフェライト系ステンレス快削鋼線材。
（２）前記鋼は、質量％で、Ｂ≦０．０１０％を含有することを特徴とする（１）に記載の鍛造性に優れるフェライト系ステンレス快削鋼線材。
（３）前記鋼は、質量％で、Ｃｕ：１．０〜４．０％を含有することを特徴とする（１）または（２）に記載の鍛造性に優れるフェライト系ステンレス快削鋼線材。
（４）前記鋼は、質量％で、Ｓｎ≦０．５０％を含有することを特徴とする（１）〜（３）のいずれか一項に記載の鍛造性に優れるフェライト系ステンレス快削鋼線材。
（５）前記鋼は、質量％で、Ｍｏ≦１．５０％を含有することを特徴とする（１）〜（４）のいずれか一項に記載の鍛造性に優れるフェライト系ステンレス快削鋼線材。
The present invention has been made to solve the above-mentioned problems. By controlling the composition of oxide inclusions, the composite inclusions of oxide and sulfide are formed and finely dispersed. As a result of the improvement, the inventors have found that by controlling the amounts and ratios of trace amounts of Al, Ca, and O, machinability can be ensured without degrading forgeability.
That is, the gist of the present invention is the following contents as described in the claims.
(1)% by mass, C ≦ 0.120%, Si: 0.1 to 2.0%, Mn: 0.1 to 3.0%, P ≦ 0.05%, S: 0.01% to 0.20%, Cr: 11.0-30.0%, N ≦ 0.250%, Al: 0.002-0.010%, Ca: 0.001-0.010%, O: 0.001 % To 0.025%, balance Fe and inevitable impurities steel, and satisfy the conditions of 0.25 ≦ Ca / Al ≦ 2.50 and 0.10 ≦ Ca / O ≦ 0.30 by mass ratio To form a composite inclusion of a CaO—SiO 2 —Al 2 O 3 type oxide having a low softening point and a sulfide of (Mn, Cr) S and having excellent forgeability Free-cutting steel wire rod.
(2) The ferritic stainless steel free-cutting steel wire excellent in forgeability as set forth in (1), wherein the steel contains mass% and B ≦ 0.010%.
(3) The ferritic stainless steel free-cutting steel wire excellent in forgeability according to (1) or (2), wherein the steel contains, by mass%, Cu: 1.0 to 4.0% .
(4) The ferritic stainless free-cutting steel excellent in forgeability according to any one of (1) to (3), wherein the steel contains, by mass%, Sn ≦ 0.50%. wire.
(5) The ferritic stainless free-cutting steel excellent in forgeability according to any one of (1) to (4), wherein the steel is contained by mass and contains Mo ≦ 1.50%. wire.
本発明による鍛造性に優れたフェライト系ステンレス快削鋼によれば鍛造加工と切削加工で効率よく部品を加工することが可能となり、部品加工の低コスト化の効果を発揮するなど産業上有用な著しい効果を奏する。 The ferritic stainless free-cutting steel with excellent forgeability according to the present invention makes it possible to process parts efficiently by forging and cutting, and is industrially useful, such as the effect of reducing the cost of part processing. There is a remarkable effect.
以下に、先ず、本発明の（１）に記載の限定理由について説明する。
Ｃ≦０．１２０％
Ｃは多量に含有させると耐食性、鍛造性、耐工具磨耗性が劣化するため上限を０．１２０％とした。好ましくは０．０４０％以下である。
Below, the limitation reason as described in (1) of this invention is demonstrated first.
C ≦ 0.120%
When C is contained in a large amount, the corrosion resistance, forgeability, and tool wear resistance deteriorate, so the upper limit was made 0.120%. Preferably it is 0.040% or less.
Ｓｉ：０．１〜２．０％
Ｓｉは脱酸剤として作用し、耐酸化性を向上させるにも有効な元素であるので０．１％以上含有させるが、必要以上の含有は鍛造性、耐工具磨耗性を劣化させるため２．０％を上限とした。好ましくは０．１〜０．４％である。
Si: 0.1 to 2.0%
Si acts as a deoxidizer and is an element effective for improving oxidation resistance, so it is contained in an amount of 0.1% or more. However, inclusion of more than necessary deteriorates forgeability and tool wear resistance. The upper limit was 0%. Preferably it is 0.1 to 0.4%.
Ｍｎ：０．１〜３．０％
ＭｎはＭｎＳとして被削性を向上させる効果があるため、０．１％以上含有させるが、過剰な含有は耐食性や靭性を低下させるためその上限を３．０％とした。好ましくは１．０〜２．５％である。
Mn: 0.1 to 3.0%
Since Mn has the effect of improving machinability as MnS, it is contained in an amount of 0.1% or more. However, excessive addition reduces the corrosion resistance and toughness, so the upper limit was made 3.0%. Preferably it is 1.0 to 2.5%.
Ｐ≦０．０５％
Ｐは含有量が多いと熱間加工性を低下させるため０．０５％を上限とした。好ましくは０．０４％以下である。
P ≦ 0.05%
When P content is large, the hot workability is lowered, so 0.05% was made the upper limit. Preferably it is 0.04% or less.
S：０．０１〜０．２０％
Ｓは被削性を改善する元素であるため０．０１％以上含有させるが、大量に含有させると硫化物を中心とした介在物が粗大化し、鍛造性が劣化する。そのため微量Ａｌ、Ｃａを添加（制御）して、低融点酸化物と硫化物の複合介在物とさせ、被削性と鍛造性を兼備させるために０．０１〜０．２０％の範囲とした。好ましくは０．０１％〜０．１０％である。
S: 0.01-0.20%
Since S is an element that improves machinability, it is contained in an amount of 0.01% or more. However, if it is contained in a large amount, inclusions centering on sulfides become coarse and forgeability deteriorates. Therefore, a small amount of Al and Ca are added (controlled) to form a composite inclusion of a low melting point oxide and sulfide, and in order to combine machinability and forgeability, the range is 0.01 to 0.20%. . Preferably, it is 0.01% to 0.10%.
図１に１７％Ｃｒ−０．０３％Ｃ−０．０２％Ｎの成分系でS量を変化させ、低融点酸化物と硫化物の複合介在物となるようにＡｌ、Ｃａ、Ｏ量を制御した本発明鋼と比較鋼の限界据込率に及ぼすＳ量の影響を示す。限界据込率の測定方法は実施例の項で述べる。一般に限界据込率が７０％以上あればヘッダー加工など鍛造において良好な作業性・生産性を示すことが知られている。図１から被削性を向上させる元素であるS量の増加によって鍛造性が低下していることが分かる。また、０．２０％Ｓ量材に介在物制御を行うと7０％の限界据込率を示した。しかし、０．２０％を超えるＳ量の材料では、介在物制御を実施しても７０％以上の限界据込率にはならなかった。この試験結果より、鍛造性を高く保つためにはS量を制限する必要がある。従ってSの上限を０．２０％とした。 In FIG. 1, the amount of Al, Ca, and O is changed so as to be a composite inclusion of a low melting point oxide and sulfide by changing the amount of S in a component system of 17% Cr-0.03% C-0.02% N. The influence of the amount of S on the limit upsetting rate of the steel of the present invention and the comparative steel controlled is shown. The method for measuring the limit upsetting rate will be described in the section of Examples. In general, it is known that if the limit upsetting ratio is 70% or more, good workability and productivity are exhibited in forging such as header processing. It can be seen from FIG. 1 that the forgeability is reduced by increasing the amount of S, which is an element improving machinability. Moreover, when inclusion control was performed on the 0.20% S amount material, a limit upsetting rate of 70% was shown. However, the material with an S amount exceeding 0.20% did not reach a limit upsetting rate of 70% or more even when inclusion control was performed. From this test result, it is necessary to limit the amount of S in order to keep the forgeability high. Therefore, the upper limit of S is set to 0.20%.
Ｃｒ：１１．０〜３０．０％
Ｃｒはマトリックスに固溶し、耐食性向上にさせる元素である。１１．０％以下では耐食性が悪くなり、多いと熱間でスケール生成を抑制し、熱間圧延疵の原因となることから、上限を３０．０％とした。好ましくは１５．０％〜１９．０％である。
Cr: 11.0-30.0%
Cr is an element that dissolves in the matrix and improves corrosion resistance. If it is 11.0% or less, the corrosion resistance is deteriorated, and if it is too much, scale formation is suppressed hot and causes hot rolling defects, so the upper limit was made 30.0%. Preferably it is 15.0%-19.0%.
Ｎ≦０．２５０％
Ｎの過度の添加は固溶強化により材料を硬質化させ、鍛造性劣化、工具寿命を低下させる。そのため上限を０．２５０％とした。好ましくは０．０１０％〜０．０３０％である。
N ≦ 0.250%
Excessive addition of N hardens the material by solid solution strengthening, and deteriorates forgeability and tool life. Therefore, the upper limit was made 0.250%. Preferably it is 0.010%-0.030%.
Ａｌ：０．００２〜０．０１０％
Ａｌは脱酸剤として作用するとともに、後述の低軟化点を有するＣａＯ−ＳｉＯ2−Ａｌ2Ｏ3系の酸化物を生成し、硫化物との複合介在物とさせ、硫化物の微細分散に重要な元素であるが、多量に含有すると硬質な粗大非金属酸化物として存在するために鍛造性を低下させる。そこで、その範囲を０．００２％以上０．０１０％以下とした。好ましくは０．００２〜０．００８％である。
Al: 0.002 to 0.010%
Al acts as a deoxidizer and generates a CaO—SiO 2 —Al 2 O 3 -based oxide having a low softening point, which will be described later, to form a composite inclusion with sulfide, thereby finely dispersing sulfide. Although it is an important element, when it is contained in a large amount, it exists as a hard coarse non-metal oxide, so that forgeability is lowered. Therefore, the range is made 0.002% to 0.010%. Preferably it is 0.002 to 0.008%.
Ｃａ：０．００１〜０．０１０％
Ｃａは低軟化点のＣａＯ−ＳｉＯ2−Ａｌ2Ｏ3系の酸化物を生成させるのに重要な元素である。Ａｌ、Ｓｉなどの脱酸元素とOの微妙なコントロールにより後述する低融点のＣａＯ−ＳｉＯ2−Ａｌ2Ｏ3系酸化物を生成し、硫化物との複合介在物として、硫化物を微細に分散させる。これらの効果を得るためには少なくとも０．００１％以上の添加が必要である。しかし、多量に含有させると、これらの効果が得られなくなることに加え、製造性も低下することから、その上限を０．０１０％とした。好ましくは０．００１〜０．００７％である。
Ca: 0.001 to 0.010%
Ca is an important element for producing a CaO—SiO 2 —Al 2 O 3 oxide having a low softening point. Low-melting CaO—SiO 2 —Al 2 O 3 -based oxides described later are produced by delicate control of deoxidizing elements such as Al and Si and O, and the sulfides are finely formed as composite inclusions with sulfides. Disperse. In order to obtain these effects, addition of at least 0.001% is necessary. However, if contained in a large amount, these effects cannot be obtained, and the manufacturability also decreases, so the upper limit was made 0.010%. Preferably it is 0.001 to 0.007%.
Ｏ：０．００１％〜０．０２５％
ＯはＡｌ、Ｃａと同じく、ＣａＯ−ＳｉＯ2−Ａｌ2Ｏ3系酸化物となり、硫化物との複合介在物として、微細に分散させるため、Ｏの含有は必須である。０．００１％以下ではその効果は小さく、０．０２５％を超えると硬質のＣｒ2Ｏ3が増大して鍛造性及び被削性を低下させるので、その範囲を０．００１％以上０．０２５％以下とした。好ましくは０．００５〜０．０２０％である。
O: 0.001% to 0.025%
O, like Al and Ca, becomes a CaO—SiO 2 —Al 2 O 3 -based oxide and is finely dispersed as a composite inclusion with sulfide, so the inclusion of O is essential. If the content is less than 0.001%, the effect is small, and if it exceeds 0.025%, hard Cr 2 O 3 increases and the forgeability and machinability deteriorate, so the range is 0.001% or more and 0.025%. % Or less. Preferably it is 0.005-0.020%.
質量比で０．２５≦Ｃａ／Ａｌ≦２．５０
ＣａＯ−ＳｉＯ2−Ａｌ2Ｏ3系の酸化物を生成させ、（Ｍｎ,Ｃｒ）Ｓの硫化物と複合介在物にするためにはＣａ／Ａｌ比をコントロールすることが必要である。Ｃａ／Ａｌ比が０．２５未満であると、ＣａＯ量が少なくなり、ＳｉＯ2−Ａｌ2Ｏ3系の酸化物が多く存在し、複合介在物になりにくくなるとともに、硬質な酸化物が多くなることから鍛造性、被削性が劣化する。また、Ｃａ／Ａｌ比が２．５０を超えると、２ＣａＯ・ＳｉＯ2が多く生成され、複合介在物になりにくくなり、複合介在物の微細化による鍛造性の向上代が低下することに加え、鋳造時にノズルが溶損し、製造性に問題が発生するため、質量比で０．２５≦Ｃａ／Ａｌ≦２．５とした。
0.25 ≦ Ca / Al ≦ 2.50 in mass ratio
In order to produce a CaO—SiO 2 —Al 2 O 3 -based oxide and make it a sulfide and a composite inclusion of (Mn, Cr) S, it is necessary to control the Ca / Al ratio. When the Ca / Al ratio is less than 0.25, the amount of CaO is reduced, there are many SiO 2 -Al 2 O 3 -based oxides, and it becomes difficult to form composite inclusions, and there are many hard oxides Therefore, forgeability and machinability deteriorate. In addition, when the Ca / Al ratio exceeds 2.50, a large amount of 2CaO · SiO 2 is generated and it becomes difficult to become a composite inclusion, and in addition to a reduction in forgeability improvement due to refinement of the composite inclusion, Since the nozzle melts at the time of casting and a problem occurs in manufacturability, 0.25 ≦ Ca / Al ≦ 2.5 is set in mass ratio.
重量比で０．１０≦Ｃａ／Ｏ≦０．３０
Ｃａ／ＯについてもＣａＯ−ＳｉＯ2−Ａｌ2Ｏ3系の酸化物を生成させ、（Ｍｎ,Ｃｒ）Ｓの硫化物と複合介在物にするためにはＣａ／Ｏ比をコントロールすることが重要である。Ｃａ／Ｏ比が０．１０未満であると、ＳｉＯ2−ＭｎＯ−Ｃｒ2Ｏ3系の酸化物が多くなり、ＣａＯ−ＳｉＯ2−Ａｌ2Ｏ3系の酸化物が少なるため、複合介在物が生成しにくくなり鍛造性が劣化する。また０．３０を超えると、ＭｎＯ量が減少し、複合介在物を生成しにくくなり鍛造性が劣化し、また鋳造時にノズルが溶損し、製造性に問題が発生するため、質量比で０．１０≦Ｃａ／Ｏ≦０．３０とした。
0.10 ≦ Ca / O ≦ 0.30 by weight ratio
For Ca / O, it is important to control the Ca / O ratio in order to produce CaO—SiO 2 —Al 2 O 3 -based oxides and to make (Mn, Cr) S sulfide and composite inclusions. It is. When the Ca / O ratio is less than 0.10, SiO 2 —MnO—Cr 2 O 3 -based oxides increase, and CaO—SiO 2 —Al 2 O 3 -based oxides decrease, resulting in complex interposition. It becomes difficult to produce things and forgeability deteriorates. On the other hand, if it exceeds 0.30, the amount of MnO decreases, it becomes difficult to form composite inclusions, the forgeability deteriorates, and the nozzle melts during casting, causing problems in manufacturability. 10 ≦ Ca / O ≦ 0.30.
ＣａＯ−ＳｉＯ2−Ａｌ2Ｏ3系酸化物
極微量のＡｌ、Ｏ、Ｃａをコントロールすることにより、（Ｍｎ,Ｃｒ）Ｓ系の硫化物の接種核として働き、複合介在物として、硫化物を微細に分散させる低融点のＣａＯ−ＳｉＯ2−Ａｌ2Ｏ3系の酸化物となり、その結果、鍛造性、被削性が向上することを見出した。
CaO—SiO 2 —Al 2 O 3 oxide By controlling trace amounts of Al, O, and Ca, it acts as an inoculation nucleus for (Mn, Cr) S sulfide, and as a composite inclusion, sulfide is added. It has been found that a low melting point CaO—SiO 2 —Al 2 O 3 -based oxide that is finely dispersed is obtained, and as a result, forgeability and machinability are improved.
図２に１７％Ｃｒ−０．０３％Ｃ−０．０２％Ｎ−０．１％Ｓ鋼のＣａ／ＡｌとＣａ／Ｏの値と鍛造性（限界据込率）の関係を示す。Ｃａ／Ａｌ、Ｃａ／Ｏの値により鍛造性が変化しており、０．２５≦Ｃａ／Ａｌ≦２．５０かつ０．１０≦Ｃａ／Ｏ≦０．３０の値では７０％以上の限界据込率を示している。 FIG. 2 shows the relationship between the Ca / Al and Ca / O values of 17% Cr-0.03% C-0.02% N-0.1% S steel and the forgeability (limit upsetting rate). The forgeability varies depending on the values of Ca / Al and Ca / O, and the limit setting is 70% or more at the values of 0.25 ≦ Ca / Al ≦ 2.50 and 0.10 ≦ Ca / O ≦ 0.30. The rate of inclusion is shown.
本発明の（２）記載の限定理由について述べる。
Ｂ≦０．０１０％
Ｂは熱間加工性や軟質化を改善するために添加される元素であり、０．００２％以上の添加により安定した効果が得られる。しかし過剰に添加するとBの化合物が析出し、熱間加工性を劣化させるので、その上限を０．０１０％とした。好ましくは０．００２〜０．００４％である。
The reason for limitation described in (2) of the present invention will be described.
B ≦ 0.010%
B is an element added to improve hot workability and softening, and a stable effect can be obtained by adding 0.002% or more. However, if added in excess, the B compound precipitates and deteriorates hot workability, so the upper limit was made 0.010%. Preferably it is 0.002 to 0.004%.
本発明の（３）記載の限定理由について述べる。
Ｃｕ：１．０〜４．０％
Ｃｕは鍛造性を改善させる重要な元素である。鍛造性を得るためには少なくとも１．０％以上の添加が必要であるが、４．０％を超えて含有すると熱間加工性が悪化することから上限を４．０％とした。好ましくは２．０〜４．０％である。
The reason for limitation described in (3) of the present invention will be described.
Cu: 1.0-4.0%
Cu is an important element for improving forgeability. In order to obtain forgeability, at least 1.0% or more is necessary. However, if the content exceeds 4.0%, the hot workability deteriorates, so the upper limit was made 4.0%. Preferably it is 2.0 to 4.0%.
本発明の（４）記載の限定理由について述べる。
Ｓｎ≦０．５０％
Ｓｎは、粒界偏析し、切削加工時の材料延性低下や潤滑性効果により切削抵抗を低減させ、切削性（表面粗度,切屑処理性，工具寿命）を向上させるのに有効な上、耐食性を劣化させる硫化物と共存させることで耐食性劣化を抑制する効果を発揮する。０．５０％を超えて添加するとその効果は飽和するばかりか、製造性を劣化させるため上限を０．５０％とする。好ましくは、０．０３〜０．３０％である。
The reason for limitation described in (4) of the present invention will be described.
Sn ≦ 0.50%
Sn is segregated at the grain boundaries and is effective in reducing cutting resistance due to material ductility reduction and lubricity effects during cutting, and improving machinability (surface roughness, chip disposal, tool life) as well as corrosion resistance. Coexisting with sulfides that degrade the corrosion resistance of the corrosion resistance. If the addition exceeds 0.50%, the effect is saturated, and the upper limit is made 0.50% in order to deteriorate manufacturability. Preferably, it is 0.03 to 0.30%.
本発明の（５）記載の限定理由について述べる。
Ｍｏ≦１．５０％
ＭｏはＣｒと同様に耐食性を向上させるのに有効な元素であり０．１％以上の添加により安定した効果が得られる。しかし、多量に添加すると熱間加工性が低下するために上限を１．５０％とした。好ましくは０．１０〜１．４０％である。
The reason for limitation described in (5) of the present invention will be described.
Mo ≦ 1.50%
Mo is an element effective for improving the corrosion resistance like Cr, and a stable effect can be obtained by addition of 0.1% or more. However, since the hot workability deteriorates when added in a large amount, the upper limit was made 1.50%. Preferably it is 0.10 to 1.40%.
また、本願発明の好ましい形態として、更に鍛造性を向上させるためには、S：０．０５％以下、Ｃ：０．０２０％以下、Ｎ：０．０２０％以下にすることが好ましく、かつその時の試験片の横断面における表層から深さ１ｍｍの間の長径２μｍ未満の硫化物、酸化物などの介在物数の割合が８０％以上であることにより、８０％以上の鍛造性を示す。表層から深さ１ｍｍの間は鍛造加工時に応力が集中するため、介在物が破壊の起点になりやすいため、介在物の大きさとその割合は重要である。２μｍ未満の介在物数の割合が少なくなると鍛造性が劣化することから、８０％以上の鍛造性を確保するためには、２μｍ未満の介在物の割合が８０％以上必要である。 Further, as a preferred embodiment of the present invention, in order to further improve forgeability, S: 0.05% or less, C: 0.020% or less, N: 0.020% or less, and at that time When the ratio of the number of inclusions such as sulfides and oxides having a major axis of less than 2 μm between the surface layer and a depth of 1 mm in the cross section of the test piece is 80% or more, forgeability of 80% or more is exhibited. Since stress concentrates at the depth of 1 mm from the surface layer at the time of forging, inclusions are likely to be the starting point of destruction, and therefore the size and the ratio of inclusions are important. Since the forgeability deteriorates when the ratio of the number of inclusions less than 2 μm decreases, the ratio of the inclusions less than 2 μm needs to be 80% or more in order to ensure forgeability of 80% or more.
これらの鋼の製造方法として、粗圧延から仕上げ圧延までの全熱間圧延工程での鋼材表面の最低温度を９５０以上１２００℃以下とし、その時の減面率を９８．０％以上にすることにより、Ａｌ、Ｃａ、Ｏの制御により微細分散させた介在物がより細かく分散し、鍛造性が更に向上することを見出した。圧延最低温度が９５０℃未満になると、Ｃａ系酸化物の軟化温度以下となり、微細に分散した介在物がさらに分断しにくくなり、更なる鍛造性の向上は期待できず、本発明の好ましい形態における鍛造性が満足されない。また、１２００℃より高くなると、粒界溶融による脆化や有害元素の完全固溶・再析出による脆化が生じやすく、製造性の問題が表れてくる。減面率は９８．０％未満であると加工による鋼中の介在物の分断が起こりにくくなるため、更なる鍛造性の向上なく、本発明の好ましい形態における鍛造性が満足されなくなる。 As a manufacturing method of these steels, the minimum temperature of the steel surface in the all hot rolling process from rough rolling to finish rolling is set to 950 to 1200 ° C., and the area reduction rate at that time is set to 98.0% or more. It was found that inclusions finely dispersed by controlling Al, Ca, and O were more finely dispersed, and the forgeability was further improved. When the minimum rolling temperature is less than 950 ° C., the Ca-based oxide is softening temperature or lower, and the finely dispersed inclusions are more difficult to break, and further improvement in forgeability cannot be expected. The forgeability is not satisfied. On the other hand, when the temperature is higher than 1200 ° C., embrittlement due to grain boundary melting and embrittlement due to complete solid solution / reprecipitation of harmful elements tend to occur, resulting in a problem in manufacturability. If the area reduction is less than 98.0%, it becomes difficult for the inclusions in the steel to be broken by the processing, so that the forgeability in the preferred embodiment of the present invention is not satisfied without further improvement in forgeability.
以下に本発明の実施例について説明する。
表1、２に本発明の実施例の化学成分と鍛造性、被削性（切屑処理性、耐工具磨耗性）の評価結果を示す。
Examples of the present invention will be described below.
Tables 1 and 2 show the evaluation results of chemical components, forgeability, and machinability (chip treatability and tool wear resistance) of the examples of the present invention.
鍛造性は圧縮試験によって得られる限界据込率によって評価した。圧縮試験は直径１１ｍｍの線材から高さ１２ｍｍ、直径８ｍｍの円柱状の試験片を作製して供試材とし、同心円状の溝をもつ拘束型ダイスでの圧縮試験により評価した。試験片の初期の高さをＨ0、割れが発生した圧縮後の高さをＨとし以下の式で求めた値を限界据込率とした。
（1−Ｈ／Ｈ0）×１００（％）
Forgeability was evaluated by the limit upsetting rate obtained by the compression test. In the compression test, a cylindrical test piece having a height of 12 mm and a diameter of 8 mm was prepared from a wire material having a diameter of 11 mm as a test material, and evaluation was performed by a compression test with a constraining die having concentric grooves. The initial height of the test piece was H 0 , the height after compression at which cracking occurred was H, and the value obtained by the following formula was defined as the limit upsetting rate.
(1-H / H 0) × 100 (%)
圧縮試験機によって歪み速度１０／ｓの一定速度で試験片を圧縮し、試験片側面の割れの有無を目視で判定し、限界据込率によって大小で評価した。
本発明鋼Ｎｏ．1〜２６は限界据込率が７０％以上であった。
The test specimen was compressed at a constant speed of 10 / s with a compression tester, the presence or absence of cracks on the side face of the specimen was visually determined, and the size was evaluated based on the limit upsetting rate.
Invention Steel No. 1 to 26 had a limit upsetting rate of 70% or more.
切削試験は直径２２ｍｍに熱間鍛伸した棒鋼を供試材として、超硬工具（Ｐ２０種）を用いて、切削速度（５０〜２００ｍ／ｍｉｎ）、切込み（０．１〜１．０ｍｍ）、送り速度（０．０１〜０．１ｍｍ／ｒｅｖ）で外周切削をおこなった。被削性の評価は切屑処理性、耐工具磨耗性にて評価した。 The cutting test uses a steel bar hot forged to a diameter of 22 mm as a test material, using a carbide tool (P20 type), cutting speed (50 to 200 m / min), cutting (0.1 to 1.0 mm), Peripheral cutting was performed at a feed rate (0.01 to 0.1 mm / rev). The machinability was evaluated based on chip disposal and tool wear resistance.
切屑処理性の評価は短く破損しているものおよび規則的ならせん状のものを○、無規則で長く繋がったものを×とした。これは、短く破損した切屑を排出するものは切削中に表面に疵をつける可能性が低いが、無規則で長く繋がった切屑は表面に疵をつけたり、工具に絡まったりするためである。本発明鋼は短く破損したものと規則的ならせん状の切屑が観察された。 In the evaluation of the chip disposability, the short-damaged and regular spiral-shaped ones were marked with ◯, and the ones that were irregularly connected for a long time were marked with ×. This is because chips that discharge short and broken chips are less likely to wrinkle the surface during cutting, but chips that are irregularly connected for a long time are wrinkled on the surface or entangled with the tool. The steel of the present invention was observed to be short and broken and regular spiral chips.
耐工具磨耗は約4000ｍ切削時の工具を観察して評価した。工具磨耗がないものは○、局所的に大きな工具磨耗が観察されるものを×とした。本発明鋼は一部微量の工具磨耗が観察されるものもあるが、大きな工具磨耗は観察されなかった。
製造性は熱間圧延後の表面疵の有無で評価した。本発明鋼については表面疵は確認されなかった。
Tool wear resistance was evaluated by observing the tool when cutting about 4000 m. The case where there was no tool wear was rated as ◯, and the case where large tool wear was observed locally was marked as x. Some of the steels of the present invention have a small amount of tool wear observed, but no significant tool wear was observed.
Manufacturability was evaluated by the presence or absence of surface defects after hot rolling. No surface flaws were observed for the inventive steel.
硫化物、酸化物などの介在物サイズ及びその数の測定は、試験片の横断面について埋め込み・鏡面研磨を行ったものについて、表層から深さ１ｍｍの間を光学顕微鏡にて１画素０．１２５μｍ観察できるカメラを用いて、４００倍で２５０視野観察し、確認された硫化物、酸化物などの介在物について圧延方向に平行の長さを測定し、その数の割合を求め評価した。最低鋼材表面温度及び減面率を制御し、Ｃａ／ＡｌとＣａ／Ｏが範囲内であり、且つS量が０．０５％以下のものは２μｍ以下の介在物数の割合が８０％以上であった。 The size of inclusions such as sulfides and oxides and the number thereof were measured by embedding and mirror-polishing the cross section of the test piece. One pixel was 0.125 μm from the surface layer to a depth of 1 mm with an optical microscope. Using a observable camera, 250 field observations were performed at 400 times, and the lengths parallel to the rolling direction were measured for the confirmed inclusions such as sulfides and oxides, and the ratio of the number was obtained and evaluated. The minimum steel surface temperature and the area reduction rate are controlled, Ca / Al and Ca / O are within the range, and the S content is 0.05% or less, the ratio of inclusions of 2 μm or less is 80% or more. there were.
引張強度はＪＩＳ９号Ａ（Ｇ.Ｌ１００ｍｍ）を用いて試験を行い引張強度を測定した。
一方、比較例Ｎｏ．２７〜４７は本発明に比べ、鍛造性、被削性（切屑処理性、耐工具磨耗性）製造性、コストのいずれかが劣っていた。
以上実施例から分かるように本発明例に優位性は明らかである。
Tensile strength was tested using JIS No. 9A (G.L100 mm) and the tensile strength was measured.
On the other hand, Comparative Example No. 27 to 47 were inferior in any of forgeability, machinability (chip disposal, tool wear resistance) manufacturability and cost as compared with the present invention.
As can be seen from the embodiments, the advantages of the present invention are clear.
以上の実施例から明らかなように、本発明により鍛造性に優れるフェライト系ステンレス快削鋼の提供が可能であり、これまで切削加工のみで複雑な形状を製造していた部品を鍛造加工と切削加工によって、材料歩留まり、生産性よく製造する上で極めて有用である。 As is clear from the above examples, the present invention can provide ferritic stainless free-cutting steel with excellent forgeability by the present invention, and forging and cutting parts that have so far been manufactured with complicated shapes only by cutting. By processing, it is extremely useful for producing materials with high yield and productivity.
Claims (5)
Ｃ≦０．１２０％、
Ｓｉ：０．１〜２．０％、
Ｍｎ０．１〜３．０％、
Ｐ≦０．０５％、
S：０．０１〜０．２０％、
Ｃｒ：１１．０〜３０．０％、
Ｎ≦０．２５０％、
Ａｌ：０．００２〜０．０１０％、
Ｃａ：０．００１〜０．０１０％、
Ｏ：０．００１％〜０．０２５％、残部Ｆｅおよび不可避的不純物からなる鋼で、かつ質量比で０．２５≦Ｃａ／Ａｌ≦２．５０および０．１０≦Ｃａ／Ｏ≦０．３０の条件を満たすことにより、低軟化点を有するＣａＯ−ＳｉＯ2−Ａｌ2Ｏ3系の酸化物と（Ｍｎ,Ｃｒ）Ｓの硫化物との複合介在物を形成することを特徴とする鍛造性に優れるフェライト系ステンレス快削鋼線材。 % By mass
C ≦ 0.120%,
Si: 0.1 to 2.0%,
Mn 0.1-3.0%,
P ≦ 0.05%,
S: 0.01-0.20%
Cr: 11.0-30.0%,
N ≦ 0.250%,
Al: 0.002 to 0.010%,
Ca: 0.001 to 0.010%,
O: Steel composed of 0.001% to 0.025%, balance Fe and inevitable impurities, and 0.25 ≦ Ca / Al ≦ 2.50 and 0.10 ≦ Ca / O ≦ 0.30 by mass ratio Forgeability characterized by forming a composite inclusion of a CaO—SiO 2 —Al 2 O 3 oxide having a low softening point and a sulfide of (Mn, Cr) S by satisfying the condition of Ferritic stainless free-cutting steel wire with excellent resistance.
The ferritic stainless steel free-cutting steel wire excellent in forgeability according to any one of claims 1 to 4, wherein the steel contains, by mass%, Mo ≦ 1.50%.
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Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN103042359A (en) * | 2012-09-11 | 2013-04-17 | 昌利锻造有限公司 | Method for forging screw for extruding machine |
| JP2013173966A (en) * | 2012-02-23 | 2013-09-05 | Nippon Steel & Sumikin Stainless Steel Corp | Ferritic free-cutting stainless steel wire rod and method for manufacturing the same |
| JP2017170579A (en) * | 2016-03-24 | 2017-09-28 | 新日鐵住金株式会社 | Outer machining method for seamless steel pipe |
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| JPH0860308A (en) * | 1994-08-11 | 1996-03-05 | Daido Steel Co Ltd | Stainless steel material excellent in wire drawability |
| JP2001011581A (en) * | 1999-06-25 | 2001-01-16 | Sanyo Special Steel Co Ltd | Free-cutting stainless steel excellent in outgassing characteristic |
| JP2001192778A (en) * | 2000-01-05 | 2001-07-17 | Sanyo Special Steel Co Ltd | High corrosion resistance free cutting stainless steel |
| JP2006097039A (en) * | 2004-09-28 | 2006-04-13 | Sanyo Special Steel Co Ltd | Free-cutting stainless steel with excellent corrosion resistance, cold forgeability and hot workability |
| JP2008240048A (en) * | 2007-03-27 | 2008-10-09 | Sanyo Special Steel Co Ltd | Stainless steel having excellent machinability |
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| JPH0860308A (en) * | 1994-08-11 | 1996-03-05 | Daido Steel Co Ltd | Stainless steel material excellent in wire drawability |
| JP2001011581A (en) * | 1999-06-25 | 2001-01-16 | Sanyo Special Steel Co Ltd | Free-cutting stainless steel excellent in outgassing characteristic |
| JP2001192778A (en) * | 2000-01-05 | 2001-07-17 | Sanyo Special Steel Co Ltd | High corrosion resistance free cutting stainless steel |
| JP2006097039A (en) * | 2004-09-28 | 2006-04-13 | Sanyo Special Steel Co Ltd | Free-cutting stainless steel with excellent corrosion resistance, cold forgeability and hot workability |
| JP2008240048A (en) * | 2007-03-27 | 2008-10-09 | Sanyo Special Steel Co Ltd | Stainless steel having excellent machinability |
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| Publication number | Priority date | Publication date | Assignee | Title |
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| JP2013173966A (en) * | 2012-02-23 | 2013-09-05 | Nippon Steel & Sumikin Stainless Steel Corp | Ferritic free-cutting stainless steel wire rod and method for manufacturing the same |
| CN103042359A (en) * | 2012-09-11 | 2013-04-17 | 昌利锻造有限公司 | Method for forging screw for extruding machine |
| JP2017170579A (en) * | 2016-03-24 | 2017-09-28 | 新日鐵住金株式会社 | Outer machining method for seamless steel pipe |
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