JPH03177537A - Steel for direct machining and induction hardening - Google Patents
Steel for direct machining and induction hardeningInfo
- Publication number
- JPH03177537A JPH03177537A JP31726889A JP31726889A JPH03177537A JP H03177537 A JPH03177537 A JP H03177537A JP 31726889 A JP31726889 A JP 31726889A JP 31726889 A JP31726889 A JP 31726889A JP H03177537 A JPH03177537 A JP H03177537A
- Authority
- JP
- Japan
- Prior art keywords
- weight
- steel
- less
- jis
- hardness
- 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
- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 45
- 239000010959 steel Substances 0.000 title claims abstract description 45
- 230000006698 induction Effects 0.000 title claims abstract description 26
- 238000003754 machining Methods 0.000 title abstract description 5
- 229910000859 α-Fe Inorganic materials 0.000 claims abstract description 14
- 239000000203 mixture Substances 0.000 claims abstract description 8
- 239000012535 impurity Substances 0.000 claims abstract description 6
- 229910001562 pearlite Inorganic materials 0.000 claims abstract description 6
- 229910052804 chromium Inorganic materials 0.000 claims abstract 2
- 239000000463 material Substances 0.000 claims description 36
- 238000005520 cutting process Methods 0.000 claims description 14
- 238000005261 decarburization Methods 0.000 claims description 6
- 229910001593 boehmite Inorganic materials 0.000 claims description 5
- FAHBNUUHRFUEAI-UHFFFAOYSA-M hydroxidooxidoaluminium Chemical compound O[Al]=O FAHBNUUHRFUEAI-UHFFFAOYSA-M 0.000 claims description 5
- 238000005096 rolling process Methods 0.000 abstract description 20
- 238000000137 annealing Methods 0.000 abstract description 3
- 230000001105 regulatory effect Effects 0.000 abstract description 3
- 229910001563 bainite Inorganic materials 0.000 abstract 1
- 229910052750 molybdenum Inorganic materials 0.000 abstract 1
- 238000007670 refining Methods 0.000 abstract 1
- 230000000694 effects Effects 0.000 description 3
- 238000010438 heat treatment Methods 0.000 description 3
- 239000002436 steel type Substances 0.000 description 3
- 238000005336 cracking Methods 0.000 description 2
- 239000013078 crystal Substances 0.000 description 2
- 238000004519 manufacturing process Methods 0.000 description 2
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 description 1
- 239000000654 additive Substances 0.000 description 1
- 230000000996 additive effect Effects 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 230000003749 cleanliness Effects 0.000 description 1
- 238000007796 conventional method Methods 0.000 description 1
- 230000003247 decreasing effect Effects 0.000 description 1
- 239000010687 lubricating oil Substances 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 230000003287 optical effect Effects 0.000 description 1
- 238000010791 quenching Methods 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、直接切削・高周波焼入用鋼材に関し、更に詳
しくは、焼なまし処理を行わずとも優れた被削性を発揮
して、圧延ままで、切削加工や転造加工を行なうことが
でき、しかも、高周波焼入性も良好で、とくに自動車の
ドライブシャフト用の素材として有用な鋼材に関する。DETAILED DESCRIPTION OF THE INVENTION (Field of Industrial Application) The present invention relates to steel materials for direct cutting and induction hardening, and more specifically, the present invention relates to steel materials for direct cutting and induction hardening. The present invention relates to a steel material that can be subjected to cutting and rolling processing while still being rolled, has good induction hardenability, and is particularly useful as a material for automobile drive shafts.
（従来の技術）
従来から、等速ジヨイントのドライブシャフトは、圧延
鋼種である５ＡＥ−１５４１に焼なまし処理または球状
化焼なまし処理を施して被削性を高めたのち、切削加工
更には転造仕上げを施し、最後に高周波焼入れを行なっ
て製造されている。(Prior Art) Conventionally, constant velocity joint drive shafts have been manufactured using rolled steel 5AE-1541 that has been annealed or spheroidized to improve its machinability, and then processed by cutting and further processing. It is manufactured by applying a rolling finish and finally induction hardening.
しかしながら、５ＡＥ−１５４１は被削性が悪く、また
加工の前段では、熱処理を施さなければならないため、
経済的に適切な素材であるとはいいがたい。However, 5AE-1541 has poor machinability and requires heat treatment before machining.
It is difficult to say that it is an economically appropriate material.
このようなことから、５ＡＥ−１５４１のＭｎ量を減少
せしめて被削性を高めた鋼種（例えばＪＩＳ規格５４０
Ｃ）も使用されているが、しかし、この鋼種は、高周波
焼入性が悪く、焼入れ後の硬化層の深さがばらつくとい
う難点がある。For this reason, steel types with improved machinability by reducing the Mn content of 5AE-1541 (for example, JIS standard 540
C) has also been used, but this steel type has the disadvantage that it has poor induction hardenability and the depth of the hardened layer after hardening varies.
（発明が解決しようとする課題）
本発明は、上記した問題を解決し、被削性が優れている
ので焼なまし処理を行なうことなく、圧延ままで切削加
工や転造仕上げが可能であり、また高周波焼入性も良好
であるため、ドライブシャフトのようなシャフト製品を
安価に製造する素材として有用な直接切削・高周波焼入
用鋼材の提供を目的とする。(Problems to be Solved by the Invention) The present invention solves the above-mentioned problems and has excellent machinability, so cutting and rolling finishing is possible without annealing. The purpose of the present invention is to provide a steel material for direct cutting and induction hardening that is useful as a material for manufacturing shaft products such as drive shafts at low cost because it also has good induction hardenability.
（課題を解決するための手段）
上記した目的を達成するために、本発明においては、
下記の組成、
Ｃ： ０．３８〜０．４５重量％、Ｓｉ：０．３５重量
％以下、 Ｍｎ ： ０．３〜１．０重量％、Ｂ：０．
０Ｏ０５〜０．００３５重量％、Ｔｉ：０．０１〜０．
０５重量％、 Ａｌ ： ０．０１〜０．０６重量％、
Ｎ：０．ＯｒＯ重量％以下、残部：Ｆｅと不可避的不純
物から成り、かつ、下記の特性、
Ｊ Ｉ ＳＧ０５５２で規定するフェライト結晶粒度番
号二６以上。(Means for Solving the Problems) In order to achieve the above object, the present invention has the following composition: C: 0.38 to 0.45% by weight, Si: 0.35% by weight or less, Mn: 0.3-1.0% by weight, B: 0.
0O05-0.0035% by weight, Ti: 0.01-0.
05% by weight, Al: 0.01-0.06% by weight,
N:0. Composed of OrO weight% or less, balance: Fe and unavoidable impurities, and has the following characteristics, ferrite crystal grain size number 26 or more as defined in J I SG0552.
ミクロ組織：フェライトとラメラ−パーライト（ただし
、ベイマイト生成量は５％以
下）、
硬さ： ＨＲＢ ８０〜９０゜
ＪＩＳＧ０５５８で規定する脱炭深さ：ＤＭ ７０．
２０ｍｍ以下、
を有することを特徴とする直接切削・高周波焼入用鋼材
と、下記の組成、
Ｃ： ０．３８〜０．４５重量％、Ｓｉ：０．３５重量
％以下、 Ｍｎ ： ０．３〜１．０重量％、Ｂ：０
．０００５〜０．００３５重量％、Ｔｉ：０．０１〜０
．０５重量％、Ａｊ７：０．０１〜０．０６重量％、Ｎ
：０．０１０重量％以下、Ｃｒ：０．３０重量％以下ま
たは／およびＭｏ：０．１０重量％以下、残部：Ｆｅと
不可避的不純物から成り、かつ、下記の特性、ＪＩＳＧ
０５５２で規定するフェライト結晶粒度番号二６以上。Microstructure: Ferrite and lamellar pearlite (however, the amount of boehmite produced is 5% or less), Hardness: HRB 80-90° Decarburization depth specified by JIS G0558: DM 70.
A steel material for direct cutting and induction hardening characterized by having a thickness of 20 mm or less, and the following composition: C: 0.38 to 0.45% by weight, Si: 0.35% by weight or less, Mn: 0.3 ~1.0% by weight, B:0
．． 0005-0.0035% by weight, Ti: 0.01-0
．． 05% by weight, Aj7: 0.01-0.06% by weight, N
: 0.010% by weight or less, Cr: 0.30% by weight or less or/and Mo: 0.10% by weight or less, balance: Fe and unavoidable impurities, and has the following properties, JISG
Ferrite crystal grain size number 26 or higher as defined by 0552.
ミクロ組織：フェライトとラメラ−パーライト（ただし
、ベイマイト生成量は５％以
下）、
硬さ： ＨＲＢ ８０〜９０゜
ＪＩＳＧ０５５８で規定する脱炭深さ：ＤＭ−Ｔ０．２
０ｍ＋ａ以下、
を有することを特徴とする直接切削・高周波焼入用鋼板
が提供される。Microstructure: Ferrite and lamellar pearlite (however, the amount of boehmite produced is 5% or less), Hardness: HRB 80-90° Decarburization depth specified by JIS G0558: DM-T0.2
Provided is a steel plate for direct cutting and induction hardening, characterized in that it has a diameter of 0 m+a or less.
本発明の鋼材の上記した特性は、直接切削性と高周波焼
入性を向上する観点から規定される。The above characteristics of the steel material of the present invention are defined from the viewpoint of improving direct machinability and induction hardenability.
すなわち、フェライト結晶粒度番号が６より小さい場合
は、鋼材の靭性不足を招くので、６以上とした。That is, if the ferrite grain size number is smaller than 6, the toughness of the steel material will be insufficient, so it is set to 6 or more.
また、ミクロ組織はフェライトとラメラ−パーライトで
構成されているが、この相内におけるベイマイトの生成
量は５％以下に制限される。ベイマイト生成量が５％よ
り多い場合は、鋼材が硬くなりすぎて、被削性の低下、
転造仕上げ時における型寿命の短縮を招くからである。Furthermore, although the microstructure is composed of ferrite and lamellar pearlite, the amount of boehmite produced within this phase is limited to 5% or less. If the amount of boeymite generated is more than 5%, the steel becomes too hard, resulting in decreased machinability.
This is because the life of the die during rolling finishing will be shortened.
硬さがＨＲＢ９０より高い場合は、鋼材の被削性の低下
と転造時の型寿命の短縮を招き、またＨＲＢ８０より低
い場合は、鋼材の強度不足と被削性の低下を招くので、
その硬さはＨＲＢ８０〜９０の範囲内に設定される。If the hardness is higher than HRB90, it will lead to a decrease in the machinability of the steel material and shorten the life of the mold during rolling, and if it is lower than HRB80, it will lead to insufficient strength of the steel material and a decrease in machinability.
Its hardness is set within the range of HRB 80 to 90.
また、脱炭深さが深すぎると、高周波焼入が充分に進行
せず硬化層の形成が不充分になると同時に、切削代も増
加するようになるので、脱炭深さはＤＭ ７０．２０
ｍｍ以下に制限される。In addition, if the decarburization depth is too deep, induction hardening will not progress sufficiently, resulting in insufficient formation of a hardened layer, and at the same time, the cutting allowance will increase, so the decarburization depth should be DM 70.20.
It is limited to less than mm.
このような特性を有する本発明の鋼材は、上記した組成
の鋼を溶製し、得られた鋼種に低温圧延を施すことによ
って製造することができる。The steel material of the present invention having such characteristics can be manufactured by melting steel having the above-mentioned composition and subjecting the obtained steel type to low-temperature rolling.
適用する低温圧延の条件は、圧延時の加熱温度２１００
℃以下、仕上げ時の温度９５０℃以下に設定される。ま
た、圧延時の減面率は７０％以上であることが好ましい
。The conditions for low-temperature rolling to be applied are a heating temperature of 2100°C during rolling.
℃ or less, and the finishing temperature is set to 950℃ or less. Moreover, it is preferable that the area reduction rate during rolling is 70% or more.
鋼材の組成において、Ｃが０．３８重量％未満の場合は
、鋼材の高周波焼入性の低下、鋼材中心部の強度不足を
招き、また０、４５重量％を超える含有量の場合は、鋼
材の被削性の低下、転造性の低下、圧延硬さの増加、高
周波焼入時における焼割感受性の増加などの不都合を招
くので、その含有量は０．３８〜０．４５重量％に設定
される。In the composition of steel materials, if C is less than 0.38% by weight, the induction hardenability of the steel material will decrease and the strength of the steel material center will be insufficient.If the C content exceeds 0.45% by weight, the steel material will deteriorate. Since it causes disadvantages such as a decrease in machinability, a decrease in formability, an increase in rolling hardness, and an increase in susceptibility to cracking during induction hardening, its content should be set at 0.38 to 0.45% by weight. Set.
Ｓｉは圧延硬さを下げるために有効な成分で、０．３５
重量％を超える含有量の場合は、圧延硬さが増大しすぎ
るので、その上限は０．３５重量％とする。Si is an effective component for lowering rolling hardness, and is 0.35
If the content exceeds 0.35% by weight, the rolling hardness increases too much, so the upper limit is 0.35% by weight.
なお、Ｓｉの含有量が少ないほど、圧延硬さは低くなる
ので、圧延硬さを更に下げる場合には、Ｓｉを０．１５
重量％以下にすることが好ましい。Note that the lower the Si content, the lower the rolling hardness, so if you want to further lower the rolling hardness, increase the Si by 0.15
It is preferable to make it less than % by weight.
Ｍｎの含有量が０．３重量％未満の場合は、鋼材の高周
波焼入性が低下すると同時に、鋼材中心部の強度不足を
招き、また１、０重量％を超えた含有量の場合は、鋼材
の被削性の低下、転造性の劣化。If the Mn content is less than 0.3% by weight, the induction hardenability of the steel material will decrease, and at the same time, it will lead to insufficient strength in the center of the steel material, and if the content exceeds 1.0% by weight, Decrease in machinability and rolling properties of steel materials.
圧延硬さの増加、高周波焼入時の焼割感受性の増大など
の不都合を招くので、その含有量は０．３〜１．０重量
％の範囲内とする。Since it causes disadvantages such as an increase in rolling hardness and an increase in susceptibility to quench cracking during induction hardening, its content is set within a range of 0.3 to 1.0% by weight.
Ｂの含有量がｏ、 ｏ ｏ ｏ ｓ重量％未満の場合は
、鋼材の高周波焼入性の低下を招き、また０、 ００３
５重量％を超えた場合は、高周波焼入性の向上効果が飽
和に達するだけではなく、熱間加工性の低下を招くよう
になるので、その含有量は０．０００５〜０、００３５
重量％の範囲内に設定される。If the content of B is less than 0,003% by weight, the induction hardenability of the steel material will decrease, and 0,003
If it exceeds 5% by weight, the effect of improving induction hardenability not only reaches saturation, but also causes a decrease in hot workability, so the content should be 0.0005 to 0.0035%.
It is set within the range of weight%.
Ｔｉ、ＡＩはいずれも鋼材中の０．Ｎを固定するための
成分であるが、その含有量が０．０１重量％より少ない
場合は、上記の効果が充分に発揮されず、また、あまり
過剰に含有せしめると鋼材の清浄度が悪化するので、Ｔ
ｉについては、０．０１〜０．０５重量％、ＡＩについ
ては、０，０１〜０，０６ｆＵｆｉ％の範囲に設定され
る。Both Ti and AI are 0.0% in steel materials. It is a component for fixing N, but if its content is less than 0.01% by weight, the above effects will not be fully exhibited, and if it is contained too much, the cleanliness of the steel material will deteriorate. Therefore, T
i is set in the range of 0.01 to 0.05% by weight, and AI is set in the range of 0.01 to 0.06fUfi%.
Ｎの含有量が０．０１０重量％を超える場合は、他の添
加成分であるＴｉと反応して生成するＴｉＮ系の非金属
介在物の量が増加して鋼材の圧延性や被削性を低下せし
めるので、その含有量は０．０１０重量％以下に規制さ
れる。If the N content exceeds 0.010% by weight, the amount of TiN-based nonmetallic inclusions that are generated by reacting with Ti, which is another additive component, increases and deteriorates the rolling properties and machinability of the steel material. Therefore, its content is regulated to 0.010% by weight or less.
また、本発明の鋼材においては、その高周波焼入性を高
めることを目的として、上記成分の外に、Ｃｒまたは／
およびＭｏを添加することが好ましい。この場合Ｃｒ、
Ｍｏを過剰に添加すると、得られた鋼材の圧延硬さが上
昇し、被削性や転造性が低下するので、Ｃｒについては
、０．３０重量％以下、Ｍｏについては０．１０重量％
に設定される。In addition, in the steel material of the present invention, in addition to the above components, Cr or /
It is preferable to add and Mo. In this case Cr,
If Mo is added excessively, the rolling hardness of the obtained steel increases and machinability and formability decrease, so Cr should be added at 0.30% by weight or less, and Mo should be added at 0.10% by weight.
is set to
なお、本発明の鋼材の被削性を一層高めるために、更に
、Ｓ：０．００５〜０．３０重量％、 Ｃａ ：０、
０００２〜０．００５重量％、Ｐｂ：０．００５〜０．
３０重量％、 Ｔｅ ： ０．００５〜０．１０重量
％のような快削性成分を必要に応じて添加することがで
きることはいうまでもない。In addition, in order to further improve the machinability of the steel material of the present invention, S: 0.005 to 0.30% by weight, Ca: 0,
0002-0.005% by weight, Pb: 0.005-0.
It goes without saying that a free machining component such as 30% by weight and Te: 0.005 to 0.10% by weight can be added as necessary.
また、本発明の鋼材には、不純物として、Ｃｒ： ０．
２０重量％以下、Ｃｕ：０．３０重量％以下。Further, the steel material of the present invention contains Cr: 0.0 as an impurity.
20% by weight or less, Cu: 0.30% by weight or less.
Ｎｉ：０．２５重量％以下、Ｍｏ：０．０３重量％以下
が含まれていてもよい。Ni: 0.25% by weight or less, Mo: 0.03% by weight or less may be contained.
（発明の実施例） 第１表に示した成分組成で各種の鋼材を溶製した。(Example of the invention) Various steel materials were melted with the compositions shown in Table 1.
（以下余白）
第１表で示した各鋼材に、加熱温度１０５０°Ｃ７仕上
げ温度８５０℃で減面率９７％の低温圧延を施し、直径
２８叩の丸棒とした。(The following is a blank space) Each of the steel materials shown in Table 1 was subjected to low-temperature rolling at a heating temperature of 1050°C and a finishing temperature of 850°C with an area reduction rate of 97% to form a round bar with a diameter of 28 strokes.
これら丸棒につき、圧延ままの状態で、下記仕様に基づ
いてフェライト結晶粒度番号、ミクロ組織、硬さ、脱皮
深さを測定し、また下記条件により被削性と高周波焼入
性を測定した。For these round bars, the ferrite grain size number, microstructure, hardness, and shedding depth were measured in the as-rolled state based on the following specifications, and the machinability and induction hardenability were also measured under the following conditions.
フェライト結晶粒度番号：ＪＩＳＧ０５５２に準拠して
測定。Ferrite grain size number: Measured according to JIS G0552.
ミクロ組織、光学顕微鏡で観察。Microstructure, observed with an optical microscope.
硬さ・ＪＩＳＺ２２４５に準拠。Hardness: Conforms to JIS Z2245.
脱皮深さ：ＪＩＳＧＯ５５８に準拠。Molting depth: Compliant with JISGO558.
切削試験：各鋼材に下記条件のドリル孔あけ加工を行な
い、切削不能となった時点
を工具寿命とし、実施例４の鋼材の
工具寿命を１００としたときの相対
値として示した。Cutting test: Each steel material was drilled under the following conditions, and the time when cutting became impossible was defined as the tool life, and the value is shown as a relative value when the tool life of the steel material of Example 4 is set to 100.
工具・５ＫＨ５１，Φ５，１）８゜
送り： ０． ｌ Ｏｍｍ／ ｒｅｖ
孔深さ：２０ｍｍ（盲孔）
速度＋ ３０ ｍ／ｍｉｎ
潤滑油：なし
高周波焼入性：鋼材を機械加工して直径２５ｍｍ長さ１
００ｍｍのテストピースと
し、これに周波数・１００ ＫＨｚ。Tool/5KH51, Φ5, 1) 8° feed: 0. l Omm/rev Hole depth: 20mm (blind hole) Speed + 30 m/min Lubricating oil: None Induction hardenability: Machined steel material to diameter 25mm length 1
00mm test piece, and set the frequency to this: 100 KHz.
出カニ６０ＫＷ、移動速度、５ ｍｍ／ｓｅｅの条件で焼入れをし、形 成された有効硬化層の深さ（ビ ッカース硬さＨＶ４００が得ら れる深さ：ｎｕｎ）を測定。Output crab 60KW, movement speed, 5 Quenched under the conditions of mm/see and shaped Depth of effective hardened layer formed (vibration) A hardness of HV400 was obtained. Measure the depth (nun).
以上の結果を一括して第２表に示した。The above results are collectively shown in Table 2.
（以下余白）
（発明の効果）
以上の説明で明らかなように、本発明の鋼材は、従来の
ように焼なまし処理を行なわなくても、圧延材のままで
、充分に良好な被削性と高周波焼入性を備えている。(The following is a blank space) (Effects of the invention) As is clear from the above explanation, the steel material of the present invention can be used as a rolled material without being annealed as in the conventional method, and can be machined in a sufficiently good manner. It has high strength and induction hardenability.
したがって、例えば自動車のドライブシャフトの製造時
にこの鋼材を用いれば、焼なまし処理を省略でき、また
切削代も低減できるので、その経済的メリットは極めて
大となる。Therefore, if this steel material is used, for example, in manufacturing drive shafts for automobiles, annealing treatment can be omitted and cutting allowances can also be reduced, resulting in extremely large economic benefits.
Claims (2)
以下、Ｍｎ：０．３〜１．０重量％、Ｂ：０．０００５
〜０．００３５重量％、Ｔｉ：０．０１〜０．０５重量
％、Ａｌ：０．０１〜０．０６重量％、Ｎ：０．０１０
重量％以下、残部：Ｆｅと不可避的不純物から成り、か
つ、下記の特性、 ＪＩＳＧ０５５２で規定するフェライト結晶粒度番号：
６以上、 ミクロ組織：フェライトとラメラ−パーライト（ただし
、ベイマイト生成量は５％以 下）、 硬さ：ＨＲＢ８０〜９０、 ＪＩＳＧ０５５８で規定する脱炭深さ： ＤＭ−Ｔ０．２０ｍｍ以下、 を有することを特徴とする直接切削・高周波焼入用鋼材
。(1) The following composition, C: 0.38 to 0.45% by weight, Si: 0.35% by weight
Below, Mn: 0.3 to 1.0% by weight, B: 0.0005
~0.0035% by weight, Ti: 0.01-0.05% by weight, Al: 0.01-0.06% by weight, N: 0.010
% by weight or less, balance: consisting of Fe and unavoidable impurities, and has the following properties, ferrite grain size number specified in JIS G0552:
6 or more, microstructure: ferrite and lamellar pearlite (however, the amount of boehmite produced is 5% or less), hardness: HRB80-90, decarburization depth specified in JIS G0558: DM-T 0.20mm or less, Characteristic steel materials for direct cutting and induction hardening.
以下、Ｍｎ：０．３〜１．０重量％、Ｂ：０．０００５
〜０．００３５重量％、Ｔｉ：０．０１〜０．０５重量
％、Ａｌ：０．０１〜０．０６重量％、Ｎ：０．０１０
重量％以下、Ｃｒ：０．３０重量％以下または／および
Ｍｏ：０．１０重量％以下、残部：Ｆｅと不可避的不純
物から成り、 かつ、下記の特性、 ＪＩＳＧ０５５２で規定するフェライト結晶粒度番号：
６以上、 ミクロ組織：フェライトとラメラ−パーライト（ただし
、ベイマイト生成量は５％以 下）、 硬さ：ＨＲＢ８０〜９０、 ＪＩＳＧ０５５８で規定する脱炭深さ： ＤＭ−Ｔ０．２０ｍｍ以下、 を有することを特徴とする直接切削・高周波焼入用鋼材
。(2) The following composition, C: 0.38 to 0.45% by weight, Si: 0.35% by weight
Below, Mn: 0.3 to 1.0% by weight, B: 0.0005
~0.0035% by weight, Ti: 0.01-0.05% by weight, Al: 0.01-0.06% by weight, N: 0.010
Weight % or less, Cr: 0.30 weight % or less or/and Mo: 0.10 weight % or less, balance: Fe and unavoidable impurities, and the following characteristics: Ferrite grain size number specified in JIS G0552:
6 or more, microstructure: ferrite and lamellar pearlite (however, the amount of boehmite produced is 5% or less), hardness: HRB80-90, decarburization depth specified in JIS G0558: DM-T 0.20mm or less, Characteristic steel materials for direct cutting and induction hardening.
Priority Applications (2)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP1317268A JPH0832946B2 (en) | 1989-12-06 | 1989-12-06 | Steel materials for direct cutting and induction hardening |
| US07/893,237 US5279688A (en) | 1989-12-06 | 1992-06-03 | Steel shaft material which is capable of being directly cut and induction hardened and a method for manufacturing the same |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP1317268A JPH0832946B2 (en) | 1989-12-06 | 1989-12-06 | Steel materials for direct cutting and induction hardening |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH03177537A true JPH03177537A (en) | 1991-08-01 |
| JPH0832946B2 JPH0832946B2 (en) | 1996-03-29 |
Family
ID=18086344
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP1317268A Expired - Lifetime JPH0832946B2 (en) | 1989-12-06 | 1989-12-06 | Steel materials for direct cutting and induction hardening |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH0832946B2 (en) |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO1994020645A1 (en) * | 1993-03-12 | 1994-09-15 | Nippon Steel Corporation | Steel material for induction-hardened shaft part and shaft part made therefrom |
| EP1857563A1 (en) * | 2005-02-25 | 2007-11-21 | Sumitomo Metal Industries, Ltd. | Non-tempered steel soft nitrided component |
| US7416616B2 (en) * | 2003-09-01 | 2008-08-26 | Sumitomo Metal Industries, Ltd. | Non-heat treated steel for soft-nitriding |
Families Citing this family (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN111549287B (en) * | 2020-06-28 | 2021-08-03 | 宝钢特钢韶关有限公司 | Medium carbon steel and production process thereof |
-
1989
- 1989-12-06 JP JP1317268A patent/JPH0832946B2/en not_active Expired - Lifetime
Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO1994020645A1 (en) * | 1993-03-12 | 1994-09-15 | Nippon Steel Corporation | Steel material for induction-hardened shaft part and shaft part made therefrom |
| EP0643148A4 (en) * | 1993-03-12 | 1995-06-14 | Nippon Steel Corp | STEEL MATERIAL FOR INDUCTION HARDENED SHAFT PART AND SHAFT PART THUS PRODUCED. |
| US7416616B2 (en) * | 2003-09-01 | 2008-08-26 | Sumitomo Metal Industries, Ltd. | Non-heat treated steel for soft-nitriding |
| EP1857563A1 (en) * | 2005-02-25 | 2007-11-21 | Sumitomo Metal Industries, Ltd. | Non-tempered steel soft nitrided component |
| EP1857563A4 (en) * | 2005-02-25 | 2010-08-04 | Honda Motor Co Ltd | Non-tempered steel soft nitrided component |
Also Published As
| Publication number | Publication date |
|---|---|
| JPH0832946B2 (en) | 1996-03-29 |
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