JP2004176175A - Steel superior in machinability and manufacturing method therefor - Google Patents
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 39
- 239000010959 steel Substances 0.000 title claims abstract description 39
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 11
- PZNSFCLAULLKQX-UHFFFAOYSA-N Boron nitride Chemical compound N#B PZNSFCLAULLKQX-UHFFFAOYSA-N 0.000 claims abstract description 28
- 238000000034 method Methods 0.000 claims abstract description 17
- 238000005096 rolling process Methods 0.000 claims abstract description 17
- 229910052717 sulfur Inorganic materials 0.000 claims abstract description 14
- 229910052796 boron Inorganic materials 0.000 claims abstract description 12
- 150000003568 thioethers Chemical class 0.000 claims abstract description 10
- 229910052799 carbon Inorganic materials 0.000 claims abstract description 7
- 230000005540 biological transmission Effects 0.000 claims abstract description 6
- 238000000605 extraction Methods 0.000 claims abstract description 6
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 4
- 238000001816 cooling Methods 0.000 claims description 14
- 239000000463 material Substances 0.000 claims description 8
- 238000005266 casting Methods 0.000 claims description 6
- 238000005098 hot rolling Methods 0.000 claims description 3
- 238000005520 cutting process Methods 0.000 abstract description 24
- 239000002244 precipitate Substances 0.000 abstract description 4
- 229910052582 BN Inorganic materials 0.000 description 21
- UCKMPCXJQFINFW-UHFFFAOYSA-N Sulphide Chemical compound [S-2] UCKMPCXJQFINFW-UHFFFAOYSA-N 0.000 description 18
- 230000003746 surface roughness Effects 0.000 description 15
- 230000000694 effects Effects 0.000 description 9
- 239000011159 matrix material Substances 0.000 description 7
- 229910000915 Free machining steel Inorganic materials 0.000 description 5
- 239000006185 dispersion Substances 0.000 description 5
- 238000005242 forging Methods 0.000 description 5
- 230000003287 optical effect Effects 0.000 description 5
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 4
- 230000000052 comparative effect Effects 0.000 description 4
- 239000002131 composite material Substances 0.000 description 4
- 229910052760 oxygen Inorganic materials 0.000 description 4
- 239000001301 oxygen Substances 0.000 description 4
- 238000001556 precipitation Methods 0.000 description 4
- 150000001875 compounds Chemical class 0.000 description 3
- 238000009826 distribution Methods 0.000 description 3
- 239000006104 solid solution Substances 0.000 description 3
- 238000007711 solidification Methods 0.000 description 3
- 230000008023 solidification Effects 0.000 description 3
- 239000000126 substance Substances 0.000 description 3
- 238000012360 testing method Methods 0.000 description 3
- 229910052718 tin Inorganic materials 0.000 description 3
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 description 2
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 description 2
- 230000015572 biosynthetic process Effects 0.000 description 2
- 239000000470 constituent Substances 0.000 description 2
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- 229910052745 lead Inorganic materials 0.000 description 2
- 238000005259 measurement Methods 0.000 description 2
- 239000000203 mixture Substances 0.000 description 2
- 229910052757 nitrogen Inorganic materials 0.000 description 2
- 229910052698 phosphorus Inorganic materials 0.000 description 2
- 239000011593 sulfur Substances 0.000 description 2
- 125000000101 thioether group Chemical group 0.000 description 2
- 230000000007 visual effect Effects 0.000 description 2
- 229910052726 zirconium Inorganic materials 0.000 description 2
- 229910017231 MnTe Inorganic materials 0.000 description 1
- 230000002411 adverse Effects 0.000 description 1
- 229910001566 austenite Inorganic materials 0.000 description 1
- 229910052797 bismuth Inorganic materials 0.000 description 1
- 238000007664 blowing Methods 0.000 description 1
- 238000009749 continuous casting Methods 0.000 description 1
- 229910052802 copper Inorganic materials 0.000 description 1
- 238000005336 cracking Methods 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 238000002425 crystallisation Methods 0.000 description 1
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- 229910052742 iron Inorganic materials 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
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- 229910052750 molybdenum Inorganic materials 0.000 description 1
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Abstract
Description
本発明は、自動車や一般機械などに用いられる鋼に関するもので、特に切削時の工具寿命と切削表面粗さおよび切り屑処理性に優れた被削性に優れた鋼に関する。 The present invention relates to steel used for automobiles, general machines, and the like, and more particularly to steel excellent in machinability, which is excellent in tool life, cutting surface roughness, and chip disposal during cutting.
一般機械や自動車は多種の部品を組み合わせて製造されているが、その部品は要求精度と製造効率の観点から、多くの場合、切削工程を経て製造されている。その際、コスト低減と生産能率の向上が求められ、鋼にも被削性の向上が求められている。特に従来ＳＵＭ２３やＳＵＭ２４Ｌは被削性を重要視して開発されてきた。これまで被削性を向上させるためにＳ，Ｐｂなどの被削性向上元素を添加するのが有効であることが知られている。しかし、需要家によってはＰｂは環境負荷として使用を避ける場合も有り、その使用量を低減する方向にある。 General machines and automobiles are manufactured by combining various types of parts, and the parts are often manufactured through a cutting process from the viewpoint of required accuracy and manufacturing efficiency. At that time, cost reduction and improvement in production efficiency are required, and steel is also required to have improved machinability. In particular, conventionally, SUM23 and SUM24L have been developed with emphasis on machinability. It has been known that it is effective to add a machinability improving element such as S or Pb in order to improve machinability. However, some customers avoid using Pb as an environmental load, and the amount of Pb used is being reduced.
これまでもＰｂを添加しない鋼の場合には、ＳのようにＭｎＳのような切削環境下で軟質となる介在物を形成して被削性を向上させる手法が使われている。しかしいわゆる低炭鉛快削鋼ＳＵＭ２４Ｌには低炭硫黄快削鋼ＳＵＭ２３と同量のＳが添加されている。したがって従来以上のＳ量を添加する必要がある。しかし、多量Ｓ添加ではＭｎＳを単に粗大にするだけで、被削性向上に有効なＭｎＳにならないだけでなく、圧延、鍛造等において破壊起点になって圧延疵等の製造上の問題を多く引き起こす。さらにＳＵＭ２３をベースとする硫黄快削鋼では構成刃先が付着しやすく、構成刃先の脱落および切り屑分離現象に伴う、切削表面に凹凸が生じ、表面粗さが劣化する。従って、被削性の観点からも表面粗さが劣化による精度低下が問題である。切り屑処理性においても、切り屑が短く分断しやすい方が良好とされているが、単なるＳ添加だけではマトリックスの延性が大きいため、十分に分断されず、大きく改善できなかった。 Until now, in the case of steel to which Pb is not added, a method of improving the machinability by forming soft inclusions such as MnS under a cutting environment such as S has been used. However, so-called low-carbon lead free-cutting steel SUM24L contains the same amount of S as low-carbon sulfur free-cutting steel SUM23. Therefore, it is necessary to add more S than before. However, the addition of a large amount of S merely increases the size of MnS, and does not not only result in MnS effective for improving machinability, but also causes a problem in rolling, forging, etc., which is a starting point of fracture and causes many manufacturing problems such as rolling flaws. . Further, in the case of the SUM23-based sulfur free-cutting steel, the constituent cutting edge easily adheres, and the cut surface becomes uneven due to the falling of the constituent cutting edge and the chip separation phenomenon, thereby deteriorating the surface roughness. Therefore, from the viewpoint of machinability, there is a problem that accuracy is reduced due to deterioration of surface roughness. In terms of chip controllability as well, it is considered better if the chips are short and easy to separate, but the simple addition of S has a large ductility of the matrix, so that the matrix is not sufficiently separated and cannot be significantly improved.
さらに、Ｓ以外の元素、Ｔｅ，Ｂｉ，Ｐ等も被削性向上元素として知られているが、ある程度の被削性を向上させることができても、圧延や熱間鍛造時に割れを生じ易くなるため、極力少ない方が望ましいとされている。 Further, elements other than S, such as Te, Bi, and P, are also known as machinability improving elements. However, even if machinability can be improved to some extent, cracks are likely to occur during rolling or hot forging. Therefore, it is considered that it is desirable to minimize the amount.
例えば、特許文献１には単独で２０μｍ以上の硫化物、あるいは複数の硫化物が略直列状に連なった長さ２０μｍ以上の硫化物郡が圧延方向断面１mm2 の視野内に３０個以上存在することによって切屑処理性を高める方法が提案されている。しかし、事実上被削性に最も有効であるサブμｍレベルの硫化物の分散については製造方法を含めて言及されておらず、またその成分系からも期待できない。
For example, in
また、特許文献２には、硫化物系介在物の平均サイズが５０μｍ2 以下であり、かつ該硫化物系介在物が１mm2 当たり７５０個以上存在することによって切屑処理性を高める方法が提案されている。しかし、事実上被削性に最も有効であるサブμｍレベルの硫化物の分散については特許文献１同様何ら言及されておらず、またそれを意識して作りこむ技術や調査する方法についても記述されていない。
Further, Patent Document 2 proposes a method for improving the chip disposability by having an average size of sulfide-based inclusions of 50 μm 2 or less and having 750 or more sulfide-based inclusions per 1 mm 2. ing. However, as in
本発明は、圧延や熱間鍛造における不具合を避けつつ、工具寿命と表面粗さの両者を改善し、従来の低炭鉛快削鋼と同等以上の被削性を有する鋼及びその製造方法を提供する。 The present invention improves both tool life and surface roughness while avoiding defects in rolling and hot forging, and provides a steel having a machinability equal to or higher than that of a conventional low-carbon lead free-cutting steel and a method for producing the same. provide.
切削は切り屑を分離する破壊現象であり、それを促進させることが一つのポイントとなる。この効果はＳを単純に増量するだけでは限界がある。本発明者らは、Ｓを増量するだけでなく、マトリックスを均一に脆化させることで破壊を容易にして工具寿命を延長するとともに切削表面の凹凸を抑制することで被削性が向上することを知見した。 Cutting is a breaking phenomenon that separates chips, and promoting it is one point. This effect is limited by simply increasing S. The present inventors not only increase the amount of S, but also enhance the machinability by suppressing the unevenness of the cutting surface by extending the tool life by facilitating the destruction by uniformly embrittlement of the matrix. Was found.
本発明は以上の知見に基づいてなされたもので、その要旨は次のとおりである。 The present invention has been made based on the above findings, and the gist is as follows.
（１）質量％で、Ｃ：０．００５〜０．２％、Ｍｎ：０．３〜３．０％、Ｓ：０．２５〜０．７５％、Ｂ：０．００２〜０．０１４％を含み、鋼材の圧延方向と平行な断面において抽出レプリカ法にて採取して透過電子顕微鏡で観察する円相当径で０．１〜０．５μｍのＭｎＳの存在密度が１０，０００個／mm2 以上であり、かつ該ＭｎＳのうち、窒化ホウ素（ＢＮ）が複合析出しているＭｎＳの個数割合が１０％以上であることを特徴とする被削性に優れる鋼。 (1) In mass%, C: 0.005 to 0.2%, Mn: 0.3 to 3.0%, S: 0.25 to 0.75%, B: 0.002 to 0.014% And the existence density of MnS having a circle equivalent diameter of 0.1 to 0.5 μm in a cross section parallel to the rolling direction of the steel material extracted by the extraction replica method and observed with a transmission electron microscope is 10,000 / mm 2. A steel excellent in machinability, characterized in that, among the MnS, the number ratio of MnS in which boron nitride (BN) is compositely precipitated is 10% or more.
（２）前記ＳおよびＢ含有量の範囲において、下記（１）式を満足する図１に示すＡ，Ｂ，Ｃ，Ｄで囲まれる領域内にあるＳおよびＢ量を含有することを特徴とする請求項１記載の被削性に優れる鋼。
(2) Within the range of the S and B contents, the S and B contents in the region surrounded by A, B, C, and D shown in FIG. 1 satisfying the following expression (1) are contained. The steel excellent in machinability according to
（Ｂ−０．００８）2／０．００６2＋(Ｓ−０．５）2／０．２５2≦１
…（１）式
（３）請求項１または２記載の鋼を、鋳造に際し、１０〜１００℃／min の冷却速度で冷却し、更に熱間圧延に際し、仕上がり温度を１０００℃以上とする圧延を実施することにより、抽出レプリカ法にて採取して透過電子顕微鏡で観察するＭｎＳに関し、鋼材の圧延方向と平行な断面において円相当径で０．１〜０．５μｍのＭｎＳの存在密度が１０，０００個／mm2 以上であり、かつ該ＭｎＳのうち、数において１０％以上の硫化物に窒化ホウ素（ＢＮ）が複合析出するようにすることを特徴とする切削性に優れる鋼の製造方法。
(B-0.008) 2 /0.006 2 + (S-0.5) 2 /0.25 2 ≦ 1
(1) Formula (3) The steel according to
以上説明したように、鋼中ＳおよびＢ量と、ＭｎＳを主成分としＢＮが複合析出した硫化物のサイズと分布を厳密に判別することにより、特に切削時の工具寿命と切削表面粗さ、および切り屑処理性の良好な被削性に優れる鋼を提供することが可能となる。 As described above, the S and B contents in steel, and the size and distribution of sulfide in which MnS is a main component and BN is compositely precipitated are strictly determined, so that tool life and cutting surface roughness, particularly during cutting, In addition, it is possible to provide steel excellent in chippability and excellent machinability.
本発明は、鉛を添加することなく十分な被削性、特に良好な表面粗さを有する鋼を得るものであり、そのために鋼に含有されるＳ量とＢ量を極力狭い領域に限定し、かつＭｎＳを光学顕微鏡では確認し得ない寸法に制御し、その微細分散の程度を従来より大幅に向上させることで良好な表面粗さと工具寿命特性を得ることを見出したものである。 The present invention is intended to obtain a steel having sufficient machinability, particularly good surface roughness, without adding lead, and therefore, it is necessary to limit the amounts of S and B contained in the steel to a narrow region as much as possible. In addition, it has been found that by controlling MnS to a size that cannot be confirmed with an optical microscope, and by improving the degree of fine dispersion significantly, a good surface roughness and tool life characteristics can be obtained.
先ず、本発明で規定する鋼の成分組成の限定理由について説明する。なお、鋼の成分組成はいずれも質量％である。 First, the reasons for limiting the composition of the steel specified in the present invention will be described. In addition, all the component compositions of steel are mass%.
Ｃは、鋼材の基本強度と鋼中の酸素量に関係するので被削性に大きな影響を及ぼす。Ｃを多量に添加して強度を高めると被削性を低下させるのでその上限を０．２％とした。一方、被削性を低下させる硬質酸化物生成を防止しつつ、凝固過程でのピンホール等の高温での固溶酸素の弊害を抑制するため、酸素量を適量に制御する必要がある。単純に吹錬によってＣ量を低減させるぎるとコストが嵩むだけでなく、鋼中酸素量が多量に残留してピンホール等の不具合の原因となる。従って、ピンホール等の不具合を容易に防止できるＣ量０．００５％を下限とした。Ｃ量の好ましい下限は０．０５％である。 C has a significant effect on machinability because it relates to the basic strength of the steel material and the amount of oxygen in the steel. If the strength is increased by adding a large amount of C, the machinability decreases, so the upper limit was made 0.2%. On the other hand, it is necessary to control the amount of oxygen to an appropriate amount in order to prevent the formation of hard oxides that reduce machinability and to suppress the adverse effects of dissolved oxygen at high temperatures such as pinholes during the solidification process. If the amount of C is simply reduced by blowing, not only the cost is increased, but also a large amount of oxygen in the steel remains and causes problems such as pinholes. Therefore, the lower limit of the C content of 0.005% at which inconveniences such as pinholes can be easily prevented is set. A preferred lower limit of the amount of C is 0.05%.
Ｍｎは、鋼中硫黄をＭｎＳとして固定・分散させるために必要である。また鋼中酸化物を軟質化させ、酸化物を無害化させるために必要である。その効果は添加するＳ量にも依存するが、０．３％以下では添加ＳをＭｎＳとして十分に固定できず、ＳがＦｅＳとなり脆くなる。Ｍｎ量が大きくなると素地の硬さが大きくなり被削性や冷間加工性が低下するので、３．０％を上限とした。 Mn is necessary for fixing and dispersing sulfur in steel as MnS. In addition, it is necessary to soften oxides in steel and make the oxides harmless. Although the effect also depends on the amount of S added, if it is 0.3% or less, the added S cannot be sufficiently fixed as MnS, and S becomes FeS and becomes brittle. When the amount of Mn increases, the hardness of the substrate increases, and machinability and cold workability decrease. Therefore, the upper limit is set to 3.0%.
Ｓは、Ｍｎと結合してＭｎＳ介在物として存在する。ＭｎＳは被削性を向上させるが、伸延したＭｎＳは鍛造時の異方性を生じる原因の一つである。大きなＭｎＳ硫化物は避けるべきであるが、被削性向上の観点からは多量の添加が好ましい。従って、ＭｎＳを微細分散させることが好ましい。Ｐｂを添加しない場合の被削性向上には０．２５％以上の添加が必要である。一方、０．７５％を越えると粗大ＭｎＳを主成分とする硫化物の生成の確率が高くなり、熱間変形特性の劣化の恐れがあるので、０．７５％を上限とした。 S bonds with Mn and exists as MnS inclusions. MnS improves machinability, but elongated MnS is one of the causes of anisotropy during forging. Large MnS sulfides should be avoided, but from the viewpoint of improving machinability, a large amount is preferable. Therefore, it is preferable to finely disperse MnS. To improve machinability when Pb is not added, it is necessary to add 0.25% or more. On the other hand, if it exceeds 0.75%, the probability of formation of sulfides containing coarse MnS as a main component increases, and there is a possibility that the hot deformation characteristics may deteriorate. Therefore, the upper limit is set to 0.75%.
Ｂは、ＢＮとして析出すると被削性向上に効果がある。特にＭｎＳと複合析出することにより研著となる。この効果は０．００２％未満では顕著でなく、０．０１４％を超えて添加すると飽和する。そこで０．００２〜０．０１４％を範囲とした。 B is effective in improving machinability when precipitated as BN. In particular, the composite precipitation with MnS results in sharpening. This effect is not remarkable at less than 0.002%, and saturates when added over 0.014%. Therefore, the range is 0.002 to 0.014%.
本発明においては、特に上述したＳ量とＢ量を極く限られた図１に示す楕円内の領域、すなわち、次の（１）式
（Ｂ−０．００８）2／０．００６2＋(Ｓ−０．５）2／０．２５2≦１
…（１）式
の領域に限定することにより最良の特性を得られる。
In the present invention, in particular, the above-described region within the ellipse shown in FIG. 1 where the S amount and the B amount are extremely limited, that is, the following equation (1) (B−0.008) 2 /0.006 2 + (S−0.5) 2 /0.25 2 ≦ 1
... The best characteristics can be obtained by limiting to the region of the expression (1).
次に、ＭｎＳの形態とそのサイズおよび分布において、円相当径にて０．１〜０．５μｍの存在密度が１０，０００個／mm2 以上と規定する理由について説明する。 Next, in the form of MnS, its size and distribution, the reason why the existence density of 0.1 to 0.5 μm in circle equivalent diameter is defined as 10,000 or more per mm 2 will be described.
ＭｎＳは被削性を向上させる介在物であり、微細に高密度で分散させることで著しく向上する。その効果を発揮するには、円相当径で０．１〜０．５μｍのＭｎＳの存在密度が１０，０００個／mm2 以上とする必要がある。通常ＭｎＳ硫化物分布は光学顕微鏡にて観察し、その寸法、密度を測定する。当該寸法のＭｎＳ硫化物は光学顕微鏡での観察では確認することが不可能なものであり、透過型電子顕微鏡（ＴＥＭ）によりはじめて観察できる。光学顕微鏡観察での寸法、密度に差は無くてもＴＥＭ観察では明確な差が認められる寸法のＭｎＳを主成分とする硫化物であり、本発明ではこれを制御し、存在形態を数値化することにより従来技術との差別化を図るものである。 MnS is an inclusion that improves machinability, and is significantly improved by finely dispersing it at high density. In order to exhibit the effect, the existence density of MnS having a circle equivalent diameter of 0.1 to 0.5 μm needs to be 10,000 / mm 2 or more. Usually, the distribution of MnS sulfide is observed with an optical microscope, and its size and density are measured. The MnS sulfide of this size cannot be confirmed by observation with an optical microscope, and can be observed only with a transmission electron microscope (TEM). It is a sulfide containing MnS as the main component and having a size that can be clearly observed in TEM observation even though there is no difference in size and density in optical microscope observation. In the present invention, this is controlled and the existence form is quantified. In this way, a differentiation from the conventional technology is achieved.
上述した寸法を超えたＭｎＳを１０，０００個／mm2 以上の密度で存在させるには本発明の範囲を超えた多量のＳの添加を必要とするが、多量添加すると粗大ＭｎＳも多数存在する確率が高くなり、鍛造時の異方性の原因となる。本発明に規定する範囲のＳ添加量でＭｎＳがこの寸法を超えると、ＭｎＳの量が不足し被削性向上に必要な密度を維持できなくなる。また、最小径０．１μｍ以下のものは実質上被削性には影響を及ぼさない。従って、円相当径にて０．１〜０．５μｍのＭｎＳの存在密度が１０，０００個／mm2 以上存在することが必要である。このＭｎＳの寸法、密度を得るためには、冷却速度の制御の他、含有するＭｎとＳの比を１．５〜２．５にするとより効果的である。 The presence of MnS exceeding the above-mentioned size at a density of 10,000 / mm 2 or more requires the addition of a large amount of S exceeding the scope of the present invention. The probability increases, which causes anisotropy during forging. If MnS exceeds this size with the amount of S added in the range specified in the present invention, the amount of MnS is insufficient, and the density required for improving machinability cannot be maintained. Further, those having a minimum diameter of 0.1 μm or less do not substantially affect the machinability. Therefore, it is necessary that the density of MnS having a circle equivalent diameter of 0.1 to 0.5 μm be present at 10,000 or more / mm 2 . In order to obtain the size and density of MnS, it is more effective to control the cooling rate and to set the ratio of Mn to S to 1.5 to 2.5.
更に、本発明においては、上述したＭｎＳにおいてその内の１０質量％以上の窒化ホウ素（ＢＮ）が複合析出した硫化物の形態を有することが重要である。 Further, in the present invention, it is important that the above-mentioned MnS has a form of sulfide in which 10% by mass or more of boron nitride (BN) is compositely precipitated.
ＢＮは通常結晶粒界に析出しやすく、マトリックスに均一に分散させることが難しい。そのため被削性向上に必要なマトリックスの均一脆化をさせることができず、ＢＮの効果を十分に発揮できない。マトリックスに均一分散させるには、ＢＮの析出サイトとなり、かつ被削性向上にも有効であるＭｎＳをマトリックスに均一に分散させることが必要である。ＢＮとＭｎＳを複合析出させることで、ＢＮの均一分散が図られ被削性は大幅に向上する。そのためには少なくとも１０％以上のＢＮがＭｎＳと複合析出している必要がある。 BN usually precipitates easily at crystal grain boundaries, and it is difficult to uniformly disperse it in a matrix. Therefore, the matrix required for improving machinability cannot be uniformly embrittled, and the effect of BN cannot be sufficiently exhibited. In order to uniformly disperse MnS in the matrix, it is necessary to uniformly disperse MnS, which serves as a BN precipitation site and is also effective in improving machinability, in the matrix. By depositing BN and MnS in combination, uniform dispersion of BN is achieved and machinability is greatly improved. For that purpose, at least 10% or more of BN needs to be compositely precipitated with MnS.
ここでいうＢＮとは、図４にＴＥＭレプリカ写真で示し、図５のＥＤＸ分析でＢとＮのピークが明瞭に認められるＢとＮの化合物を指す。 Here, BN refers to a compound of B and N which is shown in a TEM replica photograph in FIG. 4 and in which the peaks of B and N are clearly observed in the EDX analysis of FIG.
なお、ＭｎＳとは、純粋なＭｎＳのみならず、ＭｎＳを主体に含み、Ｆｅ、Ｃａ、Ｔｉ、Ｚｒ、Ｍｇ、ＲＥＭ等の硫化物がＭｎＳと固溶したり結合して共存している介在物や、ＭｎＴｅのようにＳ以外の元素がＭｎと化合物を形成してＭｎＳと固溶・結合して共存している介在物や、酸化物を核として析出した上記介在物が含まれるものであり、化学式では、（Ｍｎ，Ｘ）（Ｓ，Ｙ）（ここで、Ｘ：Ｍｎ以外の硫化物形成元素、Ｙ：Ｓ以外でＭｎと結合する元素）として表記できるＭｎ硫化物系介在物を総称して言うものである。 In addition, MnS means not only pure MnS but also intervening substances mainly containing MnS, and sulfides such as Fe, Ca, Ti, Zr, Mg, and REM coexist with MnS by solid solution or bonding. And inclusions such as MnTe in which an element other than S forms a compound with Mn to form a compound with MnS to form a solid solution / bond and coexist with the MnS, or includes the above-mentioned inclusions precipitated with an oxide as a nucleus. In the chemical formula, Mn sulfide-based inclusions that can be expressed as (Mn, X) (S, Y) (here, X: an element other than Mn and a sulfide-forming element other than Y: S that binds to Mn) are collectively referred to. That's what they say.
本発明の切削性に優れる鋼は低炭快削鋼を想定したものであるが、この鋼材には必要に応じてＣ、Ｍｎ、Ｓ、Ｂ以外の添加元素が含まれてもよい。この場合、例えば、Ｃｒ：０．０１〜２．０％、Ｖ：０．０１〜１．０％、Ｎｂ：０．００５〜０．２％、Ｍｏ：０．０１〜１．０％、Ｗ：０．０５〜１．０％、Ｎｉ：０．０５〜２．０％、Ｔｉ：０．０００５〜０．２％、Ｃａ：０．０００２〜０．０１％、Ｚｒ：０．０００５〜０．１％、Ｍｇ：０．０００３〜０．０１％、Ａｌ：０．００１〜０．１％、Ｓｉ：０．０１〜０．５％、Ｔｅ：０．０００３〜０．２％、total-Ｎ：０．００１〜０．０２％、total-Ｏ：０．０００５〜０．０３５％、Ｐ：０．００１〜０．２％、Ｚｎ：０．０００５〜０．５％、Ｓｎ：０．００５〜２．０％、Ｃｕ：０．０１〜２．０％、Ｂｉ０．００５〜０．５％、Ｐｂ：０．０１〜０．５％を１種または２種以上含有することが好ましい。尚、ＴｉはＮと化合してＴｉＮを形成するが、ＴｉＮは硬質物質で被削性を低下させる。また被削性向上に有効なＢＮを造るのに必要なＮ量を低減させる。そのためＴｉ量は０．０１０％以下が望ましい。 The steel having excellent machinability according to the present invention is assumed to be a low-carbon free-cutting steel. However, this steel material may contain additional elements other than C, Mn, S, and B as necessary. In this case, for example, Cr: 0.01 to 2.0%, V: 0.01 to 1.0%, Nb: 0.005 to 0.2%, Mo: 0.01 to 1.0%, W : 0.05-1.0%, Ni: 0.05-2.0%, Ti: 0.0005-0.2%, Ca: 0.0002-0.01%, Zr: 0.0005-0 0.1%, Mg: 0.0003-0.01%, Al: 0.001-0.1%, Si: 0.01-0.5%, Te: 0.0003-0.2%, total- N: 0.001 to 0.02%, total-O: 0.0005 to 0.035%, P: 0.001 to 0.2%, Zn: 0.0005 to 0.5%, Sn: 0. It is preferable to contain one or more of 005 to 2.0%, Cu: 0.01 to 2.0%, Bi 0.005 to 0.5%, and Pb: 0.01 to 0.5%. Note that Ti combines with N to form TiN, but TiN is a hard substance and reduces machinability. Further, the amount of N required to produce BN effective for improving machinability is reduced. Therefore, the Ti content is desirably 0.010% or less.
次に、上述したようなＭｎＳ，ＢＮを微細分散させるための鋼の製造方法について説明する。 Next, a method for producing steel for finely dispersing MnS and BN as described above will be described.
ＭｎＳを主成分としＢＮを複合析出した硫化物の微細分散は被削性向上に有効である。この硫化物を微細に分散させるにはＭｎＳを主成分としＢＮを複合析出した硫化物の晶析出を制御する必要があり、その制御には鋳造時の冷却速度範囲を規定する必要がある。冷却速度が１０℃／min 以下では凝固が遅すぎて晶出したＭｎＳを主成分としＢＮを複合析出した硫化物が粗大化してしまい、微細分散できなくなる。冷却速度が１００℃／min 以上では生成する微細硫化物の密度は飽和し、鋼片の硬度が上昇し割れの発生する危険が増す。この冷却速度を得るには鋳型断面の大きさ、鋳込み速度、鋳込み速度等を適正な値に制御することで容易に得られる。これは連続鋳造法、造塊法共に適用可能である。 Fine dispersion of a sulfide in which MnS is a main component and BN is compositely precipitated is effective for improving machinability. In order to finely disperse the sulfide, it is necessary to control the crystallization of the sulfide in which MnS is the main component and BN is compositely precipitated, and it is necessary to regulate the cooling rate range during casting for the control. If the cooling rate is 10 ° C./min or less, the solidification is too slow, and the sulfide, which is mainly composed of crystallized MnS and has BN complex precipitated, becomes coarse and cannot be finely dispersed. When the cooling rate is 100 ° C./min or more, the density of the generated fine sulfide is saturated, the hardness of the billet increases, and the risk of cracking increases. This cooling rate can be easily obtained by controlling the size of the mold section, the casting speed, the casting speed, and the like to appropriate values. This is applicable to both the continuous casting method and the ingot making method.
ここでいう冷却速度とは、鋳片厚み方向Ｑ部における液相線温度から固相線温度までの冷却時の速度のことをいう。冷却速度は凝固後の鋳片厚み方向凝固組織の２次デンドライトアームの間隔から下記式により計算で求める。 Here, the cooling rate refers to a rate at the time of cooling from the liquidus temperature to the solidus temperature in the portion Q in the slab thickness direction. The cooling rate is calculated by the following formula from the interval between the secondary dendrite arms of the solidified structure in the thickness direction of the slab after solidification.
つまり冷却条件により２次デンドライトアーム間隔が変化するので、これを測定することにより制御した冷却速度を確認できる。 That is, since the interval between the secondary dendrite arms changes depending on the cooling condition, the controlled cooling rate can be confirmed by measuring this.
ＢＮは１０００℃以上でオーステナイト中に固溶する。１０００℃以下の温度では鋳造から粗圧延過程で析出したＢＮが粒界に残留しており、ＭｎＳを主成分としＢＮを複合析出した硫化物として複合析出できない。熱間圧延時の仕上げ（最終）圧延工程で１０００℃以上の温度で圧延することで一度固溶したＢＮがＭｎＳ硫化物を析出核として複合析出しやすくなる。１０００℃以下で最終圧延を行うと、ＢＮとＭｎＳを主成分とする硫化物の複合析出は起こりにくくなる。 BN forms a solid solution in austenite at 1000 ° C. or higher. At a temperature of 1000 ° C. or lower, BN precipitated in the course of rough rolling from casting remains at the grain boundary, and cannot be precipitated as sulfide, which is mainly composed of MnS and BN is precipitated. By performing rolling at a temperature of 1000 ° C. or more in the finishing (final) rolling step in hot rolling, BN once solid-dissolved is liable to form a composite precipitate using MnS sulfide as a precipitate nucleus. When the final rolling is performed at a temperature of 1000 ° C. or lower, the composite precipitation of sulfide mainly composed of BN and MnS is less likely to occur.
本発明の効果を実施例によって説明する。 The effects of the present invention will be described with reference to examples.
表１、表２（表１のつづき１）、表３（表１のつづき２）、表４（表１のつづき３）、表５（表１のつづき４）、表６（表１のつづき５）に示す供試材は一部は２７０ｔ転炉で溶製後、冷却速度が１０〜１００℃／min になるように鋳造した。ビレットに分解圧延、さらにφ５０mmに圧延した。他は２ｔ真空溶解炉にて溶製し、φ５０mmに圧延した。このとき、鋳型断面寸法を変えることにより鋳片の冷却速度を調整した。材料の被削性は表７に条件を示すドリル穿孔試験と表８に条件を示すプランジ切削によって評価した。ドリル穿孔試験は累積穴深さ１０００mmまで切削可能な最高の切削速度（いわゆるＶＬ１０００、単位：ｍ／min ）で被削性を評価する方法である。プランジ切削は突切工具によって工具形状を転写して表面粗さを評価する方法である。その実験方法の概要を図６に示す。実験では２００溝加工した場合の表面粗さを表面粗さ計で測定した。１０点表面粗さＲｚ（単位：μｍ）を表面粗さを示す指標とした。
Table 1, Table 2 (
円相当径にて０．１〜０．５μｍの寸法のＭｎＳを主成分とする硫化物密度の測定は、φ５０mm圧延後の圧延方向と平行な断面のＱ部より抽出レプリカ法にて採取して過型電子顕微鏡にて行った。測定は１００００倍で１視野８０μｍ2 を４０視野以上行い、それを１平方ミリメートル当たりのＭｎＳを主成分とする硫化物数に換算して算出した。表２、表４および表６の（１）式計算値で１以下のものは本発明の請求項１〜３を満たしている開発鋼である。
The measurement of the sulfide density mainly composed of MnS having a size of 0.1 to 0.5 μm in a circle equivalent diameter is carried out by extracting from the Q portion of the cross section parallel to the rolling direction after φ50 mm rolling by the extraction replica method. This was performed using a scanning electron microscope. The measurement was carried out at a magnification of 10,000 times in a visual field of 80 μm 2 for 40 visual fields or more, which was converted into the number of sulfides containing MnS as a main component per 1 mm 2 . The steels having a calculated value of 1 or less in the formula (1) in Tables 2, 4 and 6 are developed
図２に本発明例のＭｎＳのＴＥＭレプリカ写真を示すとともに、図３に比較例のＭｎＳのＴＥＭレプリカ写真を示す。 FIG. 2 shows a TEM replica photograph of MnS of the present invention, and FIG. 3 shows a TEM replica photograph of MnS of the comparative example.
このように、光学顕微鏡レベルでは確認できないサイズのＭｎＳが、ＴＥＭレプリカの観察により発明例と比較例では寸法、密度に明確な差が見られる。 As described above, MnS of a size that cannot be confirmed at the optical microscope level shows a clear difference in size and density between the invention example and the comparative example by observation of the TEM replica.
なお、表２、表４、表６の切削抵抗および切り層処理性とは次のとおりである。切削抵抗は旋盤のターレットに圧電素子型工具動力計（キスラー社製）を装着、その上に工具を通常の切削と同様の位置になるようにセットして、プランジ切削して測定した。これにより工具に負荷される主分力と背分力をそれぞれ電圧信号として測定することができる。切削速度、送り速度等の切削条件は切削表面粗さを評価したものと同様である。 In addition, the cutting resistance and cut layer processing property of Table 2, Table 4, and Table 6 are as follows. The cutting resistance was measured by attaching a piezoelectric element type tool dynamometer (manufactured by Kistler) to a turret of a lathe, setting a tool on the turret at the same position as in ordinary cutting, and performing plunge cutting. As a result, the main component force and the back component force applied to the tool can be measured as voltage signals. The cutting conditions such as the cutting speed and the feed speed are the same as those for evaluating the cutting surface roughness.
切り屑処理性に関しては切り屑のカール時の曲率が小さいもの、あるいは分断されているものが好ましい。そこで切り屑が２０mmを超えた曲率半径で３巻き以上連続してカールして長く延びた切り屑を不良とした。巻数が多くとも曲率半径が小さいもの、あるいは曲率半径が大きくとも切り屑長さが１００mmに達しなかったものは良好とした。 With respect to the chip handling property, it is preferable that the chip has a small curvature at the time of curling or that the chip is divided. Accordingly, chips that were continuously curled and extended longer than three turns with a radius of curvature exceeding 20 mm were regarded as defective. If the number of windings was large and the radius of curvature was small, or if the chip length did not reach 100 mm even if the radius of curvature was large, it was regarded as good.
被削性では、発明例はいずれも比較例に対してドリル工具寿命に優れるとともに、プランジ切削における表面粗さが良好であった。特に表面粗さについては微細ＭｎＳとＢＮの複合析出の効果により非常に優れた値を得ることができた。 With respect to machinability, all of the inventive examples were superior to the comparative example in terms of the drill tool life, and the surface roughness in plunge cutting was favorable. In particular, a very excellent value of the surface roughness could be obtained due to the effect of the composite precipitation of fine MnS and BN.
Claims (3)
（Ｂ−０．００８）2／０．００６2＋(Ｓ−０．５）2／０．２５2≦１
…（１）式 The S and B contents in the range of the S and B contents, which satisfy the following expression (1), are contained in the region surrounded by A, B, C, and D shown in FIG. 1. A steel excellent in machinability according to 1.
(B-0.008) 2 /0.006 2 + (S-0.5) 2 /0.25 2 ≦ 1
... Equation (1)
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| JP2006255848A (en) * | 2005-03-18 | 2006-09-28 | Nippon Steel Corp | Cutting tool and cutting method for low carbon free-cutting steel |
| JP2007146228A (en) * | 2005-11-28 | 2007-06-14 | Nippon Steel Corp | Free cutting steel having excellent high temperature ductility |
| WO2008066194A1 (en) * | 2006-11-28 | 2008-06-05 | Nippon Steel Corporation | Free-cutting steel excellent in manufacturability |
| JP2008133503A (en) * | 2006-11-28 | 2008-06-12 | Nippon Steel Corp | Method for producing low carbon free-cutting steel with b (boron) added thereto |
| JP2014040645A (en) * | 2012-08-23 | 2014-03-06 | National Institute For Materials Science | Free-cutting iron based shape memory alloy |
| KR20150092321A (en) | 2013-02-18 | 2015-08-12 | 신닛테츠스미킨 카부시키카이샤 | Lead-containing free-machining steel |
| KR20150093816A (en) | 2013-02-18 | 2015-08-18 | 신닛테츠스미킨 카부시키카이샤 | Free machining steel with lead |
| KR101676187B1 (en) * | 2015-09-04 | 2016-11-15 | 주식회사 포스코 | Wire-shaped or rod-shaped steel having excellent cold workability and method for manufacturing same |
Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH11293391A (en) * | 1998-04-13 | 1999-10-26 | Kobe Steel Ltd | Low carbon free cutting steel excellent in chip treatability, and its production |
| JP2002249823A (en) * | 2001-02-22 | 2002-09-06 | Kawasaki Steel Corp | Method for producing free cutting steel |
-
2003
- 2003-11-04 JP JP2003374489A patent/JP4348163B2/en not_active Expired - Fee Related
Patent Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH11293391A (en) * | 1998-04-13 | 1999-10-26 | Kobe Steel Ltd | Low carbon free cutting steel excellent in chip treatability, and its production |
| JP2002249823A (en) * | 2001-02-22 | 2002-09-06 | Kawasaki Steel Corp | Method for producing free cutting steel |
Cited By (11)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2006255848A (en) * | 2005-03-18 | 2006-09-28 | Nippon Steel Corp | Cutting tool and cutting method for low carbon free-cutting steel |
| JP2007146228A (en) * | 2005-11-28 | 2007-06-14 | Nippon Steel Corp | Free cutting steel having excellent high temperature ductility |
| JP4546917B2 (en) * | 2005-11-28 | 2010-09-22 | 新日本製鐵株式会社 | Free-cutting steel with excellent hot ductility |
| WO2008066194A1 (en) * | 2006-11-28 | 2008-06-05 | Nippon Steel Corporation | Free-cutting steel excellent in manufacturability |
| JP2008133503A (en) * | 2006-11-28 | 2008-06-12 | Nippon Steel Corp | Method for producing low carbon free-cutting steel with b (boron) added thereto |
| AU2007326255B2 (en) * | 2006-11-28 | 2010-06-24 | Nippon Steel Corporation | Free-cutting steel excellent in manufacturability |
| JP5212111B2 (en) * | 2006-11-28 | 2013-06-19 | 新日鐵住金株式会社 | Free-cutting steel with excellent manufacturability |
| JP2014040645A (en) * | 2012-08-23 | 2014-03-06 | National Institute For Materials Science | Free-cutting iron based shape memory alloy |
| KR20150092321A (en) | 2013-02-18 | 2015-08-12 | 신닛테츠스미킨 카부시키카이샤 | Lead-containing free-machining steel |
| KR20150093816A (en) | 2013-02-18 | 2015-08-18 | 신닛테츠스미킨 카부시키카이샤 | Free machining steel with lead |
| KR101676187B1 (en) * | 2015-09-04 | 2016-11-15 | 주식회사 포스코 | Wire-shaped or rod-shaped steel having excellent cold workability and method for manufacturing same |
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| JP4348163B2 (en) | 2009-10-21 |
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