JPH0762220B2 - Lead free-cutting martensitic stainless steel slab and its hot rolling method - Google Patents
Lead free-cutting martensitic stainless steel slab and its hot rolling methodInfo
- Publication number
- JPH0762220B2 JPH0762220B2 JP1224196A JP22419689A JPH0762220B2 JP H0762220 B2 JPH0762220 B2 JP H0762220B2 JP 1224196 A JP1224196 A JP 1224196A JP 22419689 A JP22419689 A JP 22419689A JP H0762220 B2 JPH0762220 B2 JP H0762220B2
- Authority
- JP
- Japan
- Prior art keywords
- stainless steel
- hot rolling
- martensitic stainless
- cutting
- steel slab
- 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.)
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Description
【発明の詳細な説明】 〔産業上の利用分野〕 本発明は、SUS420J2に代表される高炭素マルテンサイト
系ステンレス鋼にPbを添加した鉛快削マルテンサイト系
ステンレス鋼鋳片、およびその熱間圧延法に関するもの
である。DETAILED DESCRIPTION OF THE INVENTION The present invention [relates] is high-carbon martensitic stainless steel added Pb to the lead free-cutting martensitic stainless steel slabs represented by SUS420J 2, and the heat It concerns a hot rolling method.
耐食性や耐熱性に優れかつ高硬度の金属材料として、SU
S420J2に代表される高炭素マルテンサイト系ステンレス
鋼があるが、このステンレス鋼は一般に粘性が大きく、
熱伝導度が悪く、切削時に切屑が工具と凝着しやすいた
め、切削加工が困難であることが多い。そこで、S,Pb,B
i,Se,Teなどの快削元素を添加して被削性を改善する研
究開発がなされた。なかでもPbとＳを複合添加した快削
ステンレス鋼は切屑処理性及び工具寿命の改善にきわめ
て有効であることから各種用途に供されるようになって
きた。As a metal material with excellent corrosion resistance and heat resistance and high hardness, SU
There is a high carbon martensitic stainless steel represented by S420J 2 , but this stainless steel generally has large viscosity,
Cutting is often difficult because the thermal conductivity is poor and the chips tend to adhere to the tool during cutting. So S, Pb, B
Research and development has been conducted to improve machinability by adding free-cutting elements such as i, Se, and Te. Among them, free-cutting stainless steel containing Pb and S added together is extremely effective in improving chip disposability and tool life, and has come to be used for various purposes.
しかしながら、この種の快削ステンレス鋼は、上記の快
削元素を添加することによって被削性は改善されるもの
の、熱間加工性が劣化するという問題点がある。特に、
本発明の対象鋼の如く熱間圧延温度域でフェライトとオ
ーステナイトの二相組織を示すステンレス鋼等において
は、もともと熱間加工性が悪い上に快削元素を添加する
ことによって熱間加工性がさらに悪くなるという問題点
があった。However, this type of free-cutting stainless steel has a problem in that although the machinability is improved by adding the above-mentioned free-cutting elements, the hot workability is deteriorated. In particular,
In the case of the stainless steel showing a two-phase structure of ferrite and austenite in the hot rolling temperature range like the target steel of the present invention, the hot workability is originally poor by adding a free-cutting element to the hot workability. There was a problem that it got worse.
Pb含有ステンレス鋼の熱間加工性劣化は以下の原因によ
っている。すなわち、Pbはステンレス鋼中への固溶度
が小さいため、ほぼ全量が最終凝固域に濃縮し晶出する
とともに、凝固後の冷却中に鋳片中で粗大化し、粒界に
Pb粒が形成される。Pb含有ステンレス鋼鋳片を1050℃
以上に加熱すると、液化したPbの膨張圧と蒸発圧により
粒界に過大な圧力が加わり熱間圧延時に粒界割れが発生
する。従って、粒界におけるPbの晶出量を低減するか、
あるいはPbを高融点化合物として液化および蒸発を防止
すると熱間加工性は改善される。The deterioration of hot workability of Pb-containing stainless steel is due to the following causes. That is, since Pb has a low solid solubility in stainless steel, almost all of it is concentrated and crystallized in the final solidification zone, and coarsens in the slab during cooling after solidification to form grain boundaries.
Pb grains are formed. 1050 ℃ for Pb-containing stainless steel slab
When heated above, excessive pressure is applied to the grain boundaries due to the expansion pressure and evaporation pressure of liquefied Pb, and grain boundary cracking occurs during hot rolling. Therefore, to reduce the amount of Pb crystallized at grain boundaries,
Alternatively, if Pb is used as a high melting point compound to prevent liquefaction and evaporation, hot workability is improved.
本発明は、熱間加工性の改善された高炭素マルテンサイ
ト系快削ステンレス鋼鋳片およびその熱間圧延法を提供
することを目的とする。An object of the present invention is to provide a high carbon martensite free cutting stainless steel slab with improved hot workability and a hot rolling method thereof.
本発明の請求項（１）は、高炭素マルテンサイト系ステ
ンレス鋼とPbと同時に適量のＳを添加することにより高
融点のPb硫化物すなわちPbS,（Mn,Pb）Ｓを生成させる
とともに、鋼中に分散して晶出させたAl2O3−SiO2系高
融点酸化物を核にしてこれら硫化物を晶出させ、その回
りにPbを晶出させ析出成長させ、粒界におけるPbの晶出
および析出量を20％以下に抑制した鋳片である。なお、
硫化物としてはこの他にMnSもあり、これも前記酸化物
を核として析出している。またPbを分散して晶出させる
ために、前記酸化物の析出量をJISポイントカウント法
に基づき0.008〜0.025％にするのが好ましい。高炭素マ
ルテンサイト系ステンレス鋼の成分限定理由はつぎのと
おりである。According to claim (1) of the present invention, a high melting point Pb sulfide, that is, PbS, (Mn, Pb) S is produced by adding an appropriate amount of S at the same time as the high carbon martensitic stainless steel and Pb. Al 2 O 3 --SiO 2 high melting point oxides dispersed and crystallized in these are used as nuclei to crystallize these sulfides, Pb is crystallized around them to cause precipitation growth, and A slab that suppresses the amount of crystallization and precipitation to 20% or less. In addition,
Other sulfides include MnS, which also deposits with the oxide as a nucleus. Further, in order to disperse and crystallize Pb, it is preferable to set the amount of the above oxide to be 0.008 to 0.025% based on the JIS point counting method. The reasons for limiting the components of the high carbon martensitic stainless steel are as follows.
Ｃは、マルテンサイトおよび炭化物を形成し、焼入れお
よび焼戻し処理後の硬さと強度を高めるのに必要な成分
であって、硬さおよび強度を得るために、0.15％以上必
要である。しかし、多すぎると冷間加工性と耐食性を劣
化させるので0.50％以下とした。C is a component that forms martensite and carbides and is required to increase hardness and strength after quenching and tempering treatment, and is required to be 0.15% or more in order to obtain hardness and strength. However, if it is too large, cold workability and corrosion resistance are deteriorated, so the content was made 0.50% or less.
Siは、鋼の溶製時における脱酸および脱硫剤として必要
である他、高融点のAl2O3−SiO2系酸化物を分散して形
成し、硫化物晶出の核とするために0.35％以上必要であ
る。このため下限を0.35％に限定する。しかし、多すぎ
るとδフェライトが生成して硬さおよび強度を減じるの
で1.0％以下とした。Si is necessary as a deoxidizing agent and a desulfurizing agent during melting of steel, and is formed by dispersing a high melting point Al 2 O 3 —SiO 2 type oxide to form a nucleus for sulfide crystallization. 0.35% or more is required. Therefore, the lower limit is limited to 0.35%. However, if it is too large, δ ferrite is formed to reduce the hardness and strength, so the content is made 1.0% or less.
Mnは、Siと同様に溶製時における脱酸および脱硫剤とし
て作用する。また、MnS,（Mn,Pb）Ｓといった硫化物を
形成し、切屑処理性および切削工具寿命を著しく改善す
る。さらに、分散して形成されたAl2O3−SiO2系酸化物
を核としてMnS,（Mn,Pb）Ｓを晶出させ、その回りにPb
を晶出させて、粒界のPb晶出および析出量を抑えるた
め、0.2％以上添加する。しかし、多すぎると熱間加工
性を害するので3.0％以下とした。Mn, like Si, acts as a deoxidizing and desulfurizing agent during melting. Further, it forms sulfides such as MnS and (Mn, Pb) S, and significantly improves chip disposability and cutting tool life. Further, MnS, (Mn, Pb) S is crystallized with Al 2 O 3 —SiO 2 type oxides formed by dispersion as nuclei, and Pb is formed around it.
Is crystallized, and 0.2% or more is added in order to suppress Pb crystallization and precipitation amount at the grain boundary. However, if it is too large, the hot workability is impaired, so the content was made 3.0% or less.
Ｓは、Mnとともに、MnS,（Mn,Pb）Ｓを形成し、またPbS
を形成して切屑処理性および切削工具寿命を著しく改善
する。このため、0.005％以上必要である。しかし、多
すぎると熱間加工性、冷間加工性および耐食性を著しく
害するので0.35％以下とした。S forms MnS, (Mn, Pb) S together with Mn, and PbS
To significantly improve chip manageability and cutting tool life. Therefore, 0.005% or more is necessary. However, if too much, the hot workability, cold workability and corrosion resistance are significantly impaired, so the content was made 0.35% or less.
Crは、耐食性、硬さ、および強度を確保するために11％
以上必要である。16％を越えて添加すると、フェライト
の生成により、焼入・焼戻し処理後の硬さ・強度が低下
する。したがって、Crは11〜16％とした。Cr is 11% to ensure corrosion resistance, hardness, and strength
The above is necessary. If it is added in excess of 16%, the hardness and strength after quenching and tempering will decrease due to the formation of ferrite. Therefore, Cr is set to 11 to 16%.
Alは、Siとともに高融点のAl2O3−SiO2系酸化物を分散
して形成し、硫化物晶出の核とするために0.003％以上
必要である。しかし、多すぎるとδフェライトが生成し
て、硬さおよび強度を減じるので0.03％以下とした。Al is required to be 0.003% or more in order to form Al 2 O 3 —SiO 2 -based oxide having a high melting point in a dispersed state together with Si and to serve as a nucleus for sulfide crystallization. However, if it is too large, δ ferrite is formed, and the hardness and strength are reduced, so the content was made 0.03% or less.
Pbは、Ｓと同様に切屑処理性および切削工具寿命を改善
する。とくに切屑処理性の改善に効果が大きい。この効
果を発揮させるには0.03％以上必要である。しかし、過
剰に添加すると、熱間加工割れが発生するので0.30％以
下とした。Pb, like S, improves chip control and cutting tool life. It is especially effective in improving the chip disposability. 0.03% or more is required to exert this effect. However, if added excessively, hot work cracking occurs, so the content was made 0.30% or less.
その他必要に応じて、耐食性、冷間圧造性等を付与する
ために、Cu,Ni,Mo等を添加することができ、残部はFeお
よび不可避的不純物からなる。In addition, Cu, Ni, Mo, etc. may be added as necessary to impart corrosion resistance, cold forging property, and the balance is Fe and inevitable impurities.
このような本発明鋳片は、粒界におけるPbの晶出および
析出成長が抑制されているので、熱間加工温度に加熱し
たとき、粒界における過大な圧力発生が防止され、熱間
加工性が改善される。Such slab of the present invention, because crystallization and precipitation growth of Pb in the grain boundary is suppressed, when heated to the hot working temperature, excessive pressure generation in the grain boundary is prevented, hot workability Is improved.
つぎに、本発明の請求項（２）の熱間圧延法は、請求項
（１）記載の鋳片を1000〜1150℃に加熱して行う。1000
℃未満では変形抵抗が大きく通常の圧延機では正常な圧
延が困難となり、1150℃を越えると、粒界のPbの影響が
現れて圧延割れが発生する。Next, the hot rolling method according to claim (2) of the present invention is performed by heating the slab according to claim (1) to 1000 to 1150 ° C. 1000
If it is less than ℃, the deformation resistance is large and normal rolling becomes difficult with a normal rolling mill. If it exceeds 1150 ℃, the effect of Pb at the grain boundary appears and rolling cracks occur.
本発明における熱間圧延としては、棒線材の連続圧延、
ストリップの連続圧延、厚板圧延、ビレットあるいはス
ラブの分塊圧延等が対象となる。As the hot rolling in the present invention, continuous rolling of a rod wire,
Continuous strip rolling, plate rolling, billet or slab lump rolling, etc. are targeted.
通常鉛快削ステンレス鋼は、Pbの膨張圧および蒸気圧に
よる粒界割れ発生を防止するために1050℃未満の温度で
圧延されるが、本発明においては、鋳片の粒界に低融点
Pbの晶出が激減しているので、熱間圧延の上限温度を11
50℃に高めることが出来る。したがって、熱間圧延作業
が容易となり、疵発生等による材料歩留りの低下が防止
される。Normally, lead free-cutting stainless steel is rolled at a temperature of less than 1050 ° C in order to prevent the occurrence of intergranular cracks due to the expansion pressure and vapor pressure of Pb, but in the present invention, it has a low melting point at the grain boundaries of the slab.
Since the crystallization of Pb is drastically reduced, the upper limit temperature of hot rolling is set to 11
Can be raised to 50 ℃. Therefore, the hot rolling work is facilitated, and the reduction in material yield due to the occurrence of defects is prevented.
表１に示す化学成分のマルテンサイト系ステンレス鋼を
溶製し、150×150mmの角鋳片に連続鋳造した。得られた
鋳片の酸化物および硫化物は、表２に示すとおりであ
る。本発明例のNo.1〜No.4は、分散して析出したAl2O3
−SiO2系酸化物（複合酸化物）を核として硫化物が晶出
し、比較例のNo.5およびNo.6は、SiO2等の酸化物が分散
しておらず、硫化物が分散されずに晶出していた。本発
明例No.1〜No.4では、Pbは酸化物を核に分散して晶出し
た硫化物の回りに主として晶出し析出成長していて、粒
界のPb量は少ない。比較例No.5およびNo.6では、Pbは硫
化物の回りにも存在するが、粒界に多く存在した。粒界
および粒内におけるPb量の割合を表２に示した。Martensitic stainless steel having the chemical composition shown in Table 1 was melted and continuously cast into a 150 × 150 mm square slab. The oxide and sulfide of the obtained cast slab are as shown in Table 2. No. 1 to No. 4 of the present invention examples are Al 2 O 3 dispersed and precipitated.
Sulfide crystallized with -SiO 2 -based oxides (composite oxides) as nuclei. In Comparative Examples No. 5 and No. 6, oxides such as SiO 2 were not dispersed, and sulfides were dispersed. It started to crystallize. In Inventive Examples No. 1 to No. 4, Pb is mainly crystallized and precipitated and grown around the sulfide crystallized by dispersing the oxide in the nucleus, and the amount of Pb in the grain boundary is small. In Comparative Examples No. 5 and No. 6, Pb was also present around the sulfides, but was abundant at the grain boundaries. Table 2 shows the proportion of Pb in the grain boundaries and in the grains.
これらの鋳片を1150℃に加熱して、直径5.5mmの線材に
連続圧延した結果、表２に示すとおり、本発明例No.1〜
No.4では圧延割れがなく、比較例No.5およびNo.6では圧
延割れが発生した。These slabs were heated to 1150 ° C. and continuously rolled into a wire rod having a diameter of 5.5 mm.
No. 4 had no rolling cracks, and Comparative Examples No. 5 and 6 had rolling cracks.
また、No.1（本発明例）およびNo.5（比較例）につい
て、鋳片を1000〜1250℃に加熱し圧延したときの割れ発
生状況を調査した。その結果、第１図に示すように、比
較例では1000〜1250℃の温度範囲において割れが発生し
ているのに対して、本発明例では加熱温度1150℃以下の
温度では圧延割れは発生しなかった。なお、第１図にお
いて、割れ評点０は割れなし、１は実用に供することが
できる程度の微細な割れ、２は皮削りを行う必要のある
もの、３以上はスクラップにせざるをえない割れであ
る。Further, with respect to No. 1 (invention example) and No. 5 (comparative example), the crack occurrence state when the slab was heated to 1000 to 1250 ° C. and rolled was investigated. As a result, as shown in FIG. 1, in the comparative example, cracking occurred in the temperature range of 1000 to 1250 ° C., whereas in the example of the present invention, rolling cracking occurred at a heating temperature of 1150 ° C. or less. There wasn't. In FIG. 1, a crack rating of 0 is no crack, 1 is a minute crack that can be put to practical use, 2 is a crack that needs to be cut, and 3 or more is a crack that must be scrapped. is there.
表１および表２に示した本発明例および比較例の各線材
について、切削性の評価を切屑処理性および工具寿命に
ついて行ったが、いずれも良好であった。また耐食性に
ついても、いずれも良好であった。With respect to each of the wire rods of the present invention example and the comparative example shown in Table 1 and Table 2, the machinability was evaluated for chip disposability and tool life, and all were good. The corrosion resistance was also good.
〔発明の効果〕 以上述べた如く、本発明によれば切削性、耐食性および
高硬度のマルテンサイト系ステンレス鋼の素材となる熱
間加工性の優れた鋳片が得られ、また製造性に優れかつ
高歩留りの熱間圧延を行うことができ、その工業的効果
は大きい。 [Effects of the Invention] As described above, according to the present invention, a slab having excellent hot workability, which is a material of martensitic stainless steel having machinability, corrosion resistance, and high hardness, can be obtained, and is excellent in manufacturability. In addition, hot rolling with high yield can be performed, and its industrial effect is great.
第１図は本発明例および比較例の熱間加工割れ状況を示
す図である。FIG. 1 is a diagram showing hot work cracking conditions of the present invention example and the comparative example.
───────────────────────────────────────────────────── フロントページの続き (72)発明者 松井 孝至 山口県光市大字島田3434番地 新日本製鐵 株式會社光製鐵所内 (56)参考文献 特開 昭63−210261（ＪＰ，Ａ) ─────────────────────────────────────────────────── ─── Continuation of the front page (72) Inventor Takashi Matsui 3434 Shimada, Hikari City, Yamaguchi Pref. Nippon Steel Co., Ltd. Inside the Hikari Works, Ltd. (56) Reference JP-A 63-210261 (JP, A)
Claims (2)
％、Mn:0.2〜3.0％、S:0.005〜0.35％、Cr:11〜16％、A
l:0.003〜0.03％、Pb:0.03〜0.30％を含有し、残部鉄お
よび不可避的不純物からなり、かつ粒界におけるPbの晶
出・析出量の割合が20％以下であることを特徴とする鉛
快削マルテンサイト系ステンレス鋼鋳片。1. C: 0.15 to 0.50% by weight%, Si: 0.35 to 1.0
%, Mn: 0.2 to 3.0%, S: 0.005 to 0.35%, Cr: 11 to 16%, A
l: 0.003 to 0.03%, Pb: 0.03 to 0.30%, characterized by the balance iron and unavoidable impurities, and the proportion of Pb crystallized / precipitated at grain boundaries is 20% or less. Lead free-cutting martensitic stainless steel slab.
し熱間圧延することを特徴とする鉛快削マルテンサイト
系ステンレス鋼鋳片の熱間圧延法。2. A hot rolling method for lead free-cutting martensitic stainless steel slab, comprising heating the slab according to claim 1 to 1000 to 1150 ° C. and hot rolling.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP1224196A JPH0762220B2 (en) | 1989-08-30 | 1989-08-30 | Lead free-cutting martensitic stainless steel slab and its hot rolling method |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP1224196A JPH0762220B2 (en) | 1989-08-30 | 1989-08-30 | Lead free-cutting martensitic stainless steel slab and its hot rolling method |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH0387337A JPH0387337A (en) | 1991-04-12 |
| JPH0762220B2 true JPH0762220B2 (en) | 1995-07-05 |
Family
ID=16810029
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP1224196A Expired - Fee Related JPH0762220B2 (en) | 1989-08-30 | 1989-08-30 | Lead free-cutting martensitic stainless steel slab and its hot rolling method |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH0762220B2 (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN107699811A (en) * | 2017-09-08 | 2018-02-16 | 中国科学院合肥物质科学研究院 | A kind of silica dispersion-strengthened steel and preparation method thereof |
Families Citing this family (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN113787094B (en) * | 2021-08-17 | 2024-02-02 | 首钢集团有限公司 | Rolling method of high-carbon free-cutting steel wire rod |
Family Cites Families (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2742578B2 (en) * | 1986-09-08 | 1998-04-22 | 愛知製鋼株式会社 | High hardness stainless steel for cold forging |
| JPH0756064B2 (en) * | 1987-02-27 | 1995-06-14 | 大同特殊鋼株式会社 | Martensite free cutting stainless steel |
-
1989
- 1989-08-30 JP JP1224196A patent/JPH0762220B2/en not_active Expired - Fee Related
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN107699811A (en) * | 2017-09-08 | 2018-02-16 | 中国科学院合肥物质科学研究院 | A kind of silica dispersion-strengthened steel and preparation method thereof |
Also Published As
| Publication number | Publication date |
|---|---|
| JPH0387337A (en) | 1991-04-12 |
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