JPH02217437A - Steel for cold working - Google Patents
Steel for cold workingInfo
- Publication number
- JPH02217437A JPH02217437A JP4073689A JP4073689A JPH02217437A JP H02217437 A JPH02217437 A JP H02217437A JP 4073689 A JP4073689 A JP 4073689A JP 4073689 A JP4073689 A JP 4073689A JP H02217437 A JPH02217437 A JP H02217437A
- Authority
- JP
- Japan
- Prior art keywords
- steel
- cold working
- less
- content
- grain
- 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.)
- Pending
Links
- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 28
- 239000010959 steel Substances 0.000 title claims abstract description 28
- 238000005482 strain hardening Methods 0.000 title claims abstract description 12
- 239000012535 impurity Substances 0.000 claims abstract description 8
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 6
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 5
- 229910052759 nickel Inorganic materials 0.000 claims abstract description 5
- 229910052796 boron Inorganic materials 0.000 claims abstract description 4
- 229910052757 nitrogen Inorganic materials 0.000 claims abstract description 4
- 229910052782 aluminium Inorganic materials 0.000 claims abstract 3
- 229910052799 carbon Inorganic materials 0.000 claims abstract 3
- 238000000034 method Methods 0.000 abstract description 11
- 239000000203 mixture Substances 0.000 abstract description 10
- 238000010791 quenching Methods 0.000 abstract description 9
- 230000000171 quenching effect Effects 0.000 abstract description 7
- 230000006866 deterioration Effects 0.000 abstract description 5
- 238000010438 heat treatment Methods 0.000 abstract description 4
- 229910052758 niobium Inorganic materials 0.000 abstract description 4
- 229910052698 phosphorus Inorganic materials 0.000 abstract description 2
- 229910052748 manganese Inorganic materials 0.000 abstract 2
- 230000001105 regulatory effect Effects 0.000 abstract 1
- 229910052720 vanadium Inorganic materials 0.000 abstract 1
- 230000000694 effects Effects 0.000 description 18
- 238000007670 refining Methods 0.000 description 6
- 239000013078 crystal Substances 0.000 description 4
- 229920006395 saturated elastomer Polymers 0.000 description 4
- 229910000851 Alloy steel Inorganic materials 0.000 description 3
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 3
- 229910001566 austenite Inorganic materials 0.000 description 3
- 238000000137 annealing Methods 0.000 description 2
- 238000005336 cracking Methods 0.000 description 2
- 238000004519 manufacturing process Methods 0.000 description 2
- 239000000463 material Substances 0.000 description 2
- 239000002244 precipitate Substances 0.000 description 2
- 238000005204 segregation Methods 0.000 description 2
- 229910045601 alloy Inorganic materials 0.000 description 1
- 239000000956 alloy Substances 0.000 description 1
- 238000009749 continuous casting Methods 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 239000004615 ingredient Substances 0.000 description 1
- 229910052742 iron Inorganic materials 0.000 description 1
- 238000004881 precipitation hardening Methods 0.000 description 1
- 239000000047 product Substances 0.000 description 1
- 230000000087 stabilizing effect Effects 0.000 description 1
- 238000005496 tempering Methods 0.000 description 1
- 238000010998 test method 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)
この発明は、冷間での成型後、焼入れ、焼戻し処理を行
う機械構造用部品、例えばシャフト、歯車、ボルトなど
に使用される冷間加工用鋼に関する。Detailed Description of the Invention (Industrial Application Field) This invention relates to cold processing used for mechanical structural parts, such as shafts, gears, bolts, etc., which are subjected to quenching and tempering after cold forming. Regarding industrial steel.
(従来の技術)
一般に、機械構造用として使用されている、例えば0.
35%C−1,0%Cr−0,2%Moの組成を有する
JIS G4105に規定されているSCM435の低
合金鋼や、0.31%C−0,8%Cr−1,8%Ni
−0,2%Moの組成を有するJTS G4103に規
定されたSNCM431の低合金鋼、あるいは0.2%
C−0,8%Cr−0,02%Bの組成を有するボロン
調などにおいては、製造工程の合理化や仕上精度向上を
目的として、冷間加工による成型が行われている。しか
し、この冷間加工時に強加工が加わる部位では、次の焼
入れ時にオーステナイト結晶粒(以下、1粒という)が
粗大化し、機械的性質、特に衝撃特性の劣化や熱処理歪
の増大などの問題が生じるため、1粒の粗大化を防止す
る必要がある。(Prior Art) Generally, for example, 0.05 mm is used for mechanical structures.
SCM435 low alloy steel specified in JIS G4105 with a composition of 35%C-1,0%Cr-0,2%Mo, 0.31%C-0,8%Cr-1,8%Ni
- SNCM431 low alloy steel specified in JTS G4103 with a composition of 0.2% Mo, or 0.2% Mo
Boron tone having a composition of C-0.8% Cr-0.02% B is formed by cold working for the purpose of streamlining the manufacturing process and improving finishing accuracy. However, in areas where heavy working is applied during cold working, austenite crystal grains (hereinafter referred to as 1 grain) become coarse during the subsequent quenching, resulting in problems such as deterioration of mechanical properties, especially impact properties, and increased heat treatment distortion. Therefore, it is necessary to prevent one grain from becoming coarse.
これに対して、従来下記のような技術が対策として用い
られ、あるいは提案されている。In response to this, the following techniques have been conventionally used or proposed as countermeasures.
(1)特公昭55−38010号公報に提案されている
ようにNbを0.005〜0.080%添加し、特殊な
精錬処理を行う方法、及び特開昭56−75551号公
報、特公昭63−11423号公報に提案されているA
lとNの比(Ai<χ)IN(χ))を限定する方法な
ど、成分を限定することにより1粒の粗大化を防止する
技術。(1) A method of adding 0.005 to 0.080% Nb and performing a special refining treatment as proposed in Japanese Patent Publication No. 55-38010, and a method of adding 0.005 to 0.080% Nb and performing a special refining treatment, as proposed in Japanese Patent Publication No. 56-75551, A proposed in Publication No. 63-11423
Techniques to prevent coarse grains by limiting the ingredients, such as limiting the ratio of l to N (Ai<χ)IN(χ).
(2)鉄と鋼、 Vol、70(1984) p、19
93〜2000に記載されているように、焼入れ処理を
行う前に焼なましもしくは焼ならしを行う技術。(2) Iron and Steel, Vol. 70 (1984) p. 19
93-2000, a technique of performing annealing or normalizing before hardening treatment.
(発明が解決しようとする!I!!!I)しかしながら
、上記(1)の成分を限定することによりγ粒の粗大化
を防止する技術においゼは、冷間での加工の際、圧下率
70%もしくはそれ以上の加工を加えた場合、Wbの添
加、あるいは八l(χ)IN(χ)比の限定をそれぞれ
個別に行っても1粒の粗大化を防止することは難しく、
かつ、前者においては特殊な精錬処理を伴うこともあっ
てコスト的に不利である。また、(2)の焼入れ処理を
行う前に焼なましもしくは焼ならしを行う技術において
は、γ粒の粗大化防止は可能であるが、製造コストが嵩
むという問題がある。(This is what the invention attempts to solve!I!!!I) However, the technology for preventing the coarsening of γ grains by limiting the components mentioned in (1) above is difficult to achieve when the reduction rate is reduced during cold processing. When processed by 70% or more, it is difficult to prevent one grain from becoming coarse even if Wb is added or the 8l(χ)IN(χ) ratio is individually limited.
Moreover, the former method is disadvantageous in terms of cost since it may involve special refining treatment. Further, in the technique (2) of performing annealing or normalizing before performing the quenching treatment, it is possible to prevent the γ grains from becoming coarse, but there is a problem in that the manufacturing cost increases.
本発明は、冷間で強加工を加えた場合でもその後の焼入
れで1粒が粗大化しない冷間加工用鋼を低コストで作る
ことを目的とする。An object of the present invention is to produce, at low cost, a steel for cold working that does not cause grain coarsening during subsequent quenching even when subjected to strong cold working.
(課題を解決するための手段)
上記の目的を達成するため、本発明者等は冷間での強加
工後の焼入れ時における1粒の粗大化防止に必要なNb
、 iの含有量、それらと反応して析出物を形成する
N量及びそれらの量的なバランスについて検討を重ねた
結果、下記の3点が上記目的を達成する上で重要である
ことを知見した。(Means for Solving the Problems) In order to achieve the above object, the present inventors have developed the Nb
As a result of repeated studies on the content of i, the amount of N that reacts with them to form precipitates, and their quantitative balance, we found that the following three points are important in achieving the above objectives. did.
即ち、
(1) ^l単独では、粗粒化を防止することはでき
ない。That is, (1) ^l alone cannot prevent grain coarsening.
(2) Nbを含有させることにより、粗粒化を抑制
することは可能である。(2) By containing Nb, it is possible to suppress grain coarsening.
(3)粗粒化を完全に防止するには、Nbを含有させる
と共にAi(χ)IN(χ)の比を1.0θ〜2.00
にする必要がある。(3) To completely prevent grain coarsening, Nb should be included and the ratio of Ai(χ)IN(χ) should be 1.0θ to 2.00.
It is necessary to
本発明は上記知見に基づいてなされたものであって、そ
の要旨は下記■及び■の組成をもつ冷間加工用鋼にある
。(以下、%は全で重量%を意味する。)
■ C: 0.30〜0.50% St : 0.
50%以下Mn ; 0.50%未満 Cr :
0.1〜5.0%Mo : 0.01〜0.80%
Nb : 0.005〜0.20%八〇 : へ、
005〜0.10% N : 0.035%以下(た
だし1.00≦^1(χ)IN(χ)≦2.00)残部
:Fe及び不可避的不純物。The present invention has been made based on the above findings, and its gist lies in a cold working steel having the following compositions (1) and (2). (Hereinafter, % means weight % in total.) ■ C: 0.30 to 0.50% St: 0.
50% or less Mn; less than 0.50% Cr:
0.1~5.0%Mo: 0.01~0.80%
Nb: 0.005-0.20% 80: To,
005-0.10% N: 0.035% or less (however, 1.00≦^1(χ)IN(χ)≦2.00) Remainder: Fe and inevitable impurities.
■ 上記■の成分に加えて更に
V : 0.01〜0.30%、B : 0.0003
〜0.0050%、Ni : 0.01〜2.00%
め−3元素のうちから選ばれた1種以上の成分を含有す
るもの。■ In addition to the above component ■, V: 0.01-0.30%, B: 0.0003
~0.0050%, Ni: 0.01~2.00% Me - Contains one or more components selected from the three elements.
上記何れの組成でも、不純物としてのPは0.015%
以下、Sは0.01%以下とする。In any of the above compositions, P as an impurity is 0.015%
Hereinafter, S shall be 0.01% or less.
(作用)
以下に、本発明の綱を構成する各成分の作用効果上それ
らの含有量の限定理由について述べる。(Function) Below, the reason for limiting the content of each component constituting the group of the present invention will be described in terms of the function and effect.
Cは鋼の焼入性を上げて強度を増加させ、かつ結晶粒の
微細化のためにも有効な成分である。その含有量が0.
30%未満では、焼入性向上の効果が小さい、一方、0
.50%を超えて含有させると焼入れ時の焼割れ感受性
が増加し、また、他の合金成分と関連して靭性劣化をも
招くことから、その含有量を0.30〜0.50%とし
た。C is an effective component for improving the hardenability of steel, increasing its strength, and also for refining crystal grains. Its content is 0.
If it is less than 30%, the effect of improving hardenability is small;
.. If the content exceeds 50%, the susceptibility to quench cracking during quenching increases, and it also causes toughness deterioration in association with other alloy components, so the content was set at 0.30 to 0.50%. .
Siは鋼の脱酸及び強度増加のために有効な元素である
が、0.50%を超えると偏析して靭性の劣化をきたす
場合があるので、その含有量を0.50%以下とした。Si is an effective element for deoxidizing steel and increasing its strength, but if it exceeds 0.50%, it may segregate and deteriorate toughness, so its content was set to 0.50% or less. .
Mnは脱酸の他、焼入性向上に有効な元素であるが、偏
析により粒界を詭化し靭性の劣化を生じさせるため、そ
の含有量を0.50%未満とした。Mn is an effective element for improving hardenability in addition to deoxidizing, but its content is set to less than 0.50% because it causes segregation in grain boundaries and deterioration in toughness.
Crは鋼の焼入性を向上するのに有効な元素であるが、
0.1%未満ではその効果は得られず、5.0%を超え
ると靭性の劣化、及び焼割れ感受性の増大をきたすため
、その含有量を0゜1〜5.0%とした。Cr is an effective element for improving the hardenability of steel, but
If it is less than 0.1%, the effect cannot be obtained, and if it exceeds 5.0%, the toughness deteriorates and the susceptibility to quench cracking increases, so the content was set to 0.1 to 5.0%.
Moは鋼の焼入性を向上するのに有効な元素であるが、
0.01%未満では効果は得られず、0.8%を超えて
含有させてもその効果は飽和し、コストの上昇を招くだ
けであるため、その含有量を0.01〜0.80%とし
た。Mo is an effective element for improving the hardenability of steel, but
If the content is less than 0.01%, no effect will be obtained, and if the content exceeds 0.8%, the effect will be saturated and the cost will increase, so the content should be reduced from 0.01 to 0.80. %.
Nbは本発明において重要な元素の一つであり、鋼の強
度、靭性を向上させるとともに結晶粒を微細化しかつ結
晶の粗粒化を防止するのに有効な元素である。しかし、
その効果を確保するためにはo、 oos%以上含有さ
せることが必要であり、一方、0.20%を超えて含有
させてもその効果は飽和しコストの増加を招くだけであ
るから、その含有量をo、oos〜0.20%とした。Nb is one of the important elements in the present invention, and is an effective element for improving the strength and toughness of steel, refining crystal grains, and preventing grain coarsening. but,
In order to ensure the effect, it is necessary to contain o, oos% or more.On the other hand, if the content exceeds 0.20%, the effect will be saturated and the cost will only increase. The content was set to o, oos ~ 0.20%.
^lは鋼の脱酸の安定化、均質化及び細粒化に有効な元
素であるが、0.005%未満では十分゛な効果は得ら
れず、一方、0.10%を超えて含有させてもその効果
は飽和することより、その含有量をo、oos〜0,1
0%とした。^l is an effective element for stabilizing, homogenizing, and refining the deoxidation of steel, but if it is less than 0.005%, sufficient effects cannot be obtained; on the other hand, if it is contained more than 0.10%, Even if the content is o, oos ~ 0,1, the effect is saturated.
It was set to 0%.
Nも本発明において重要な元素の一つであり、Nb、A
ffi等と結合して析出物を生成し、それが結晶粒の粗
大化防止に寄与する。しかし、低合金鋼においては0.
035%を超えて含有させることは難しいため、その含
有量を0.035%以下とした。N is also one of the important elements in the present invention, and Nb, A
It combines with ffi and the like to form precipitates, which contribute to preventing coarsening of crystal grains. However, in low alloy steel, 0.
Since it is difficult to contain more than 0.035%, the content was set to 0.035% or less.
一方、A1.とNの含有量のバランスについて、前記の
式を満たすように定めたのは、後述の実施例で示すよう
に、冷間で70%以上の強加工を加えても次工程の焼入
れ時に1粒の粗大化を生じさせないためには、少なくと
もA Il、(X)/N (χ)比が前記の式を満たす
ことが必要であるからである。On the other hand, A1. Regarding the balance between the content of This is because, in order to prevent coarsening of the ratio, it is necessary that at least the ratio of A Il, (X)/N (χ) satisfies the above formula.
本発明鋼の一つは上記の成分以外、残部Fθと不可避の
不純物から成るものである。不純物としてはPとSの上
限を抑えることが重要である。One of the steels of the present invention consists of the above-mentioned components and the remainder Fθ and unavoidable impurities. It is important to suppress the upper limits of P and S as impurities.
Pはいかなる熱処理を施してもその粒界偏析を完全に消
滅することはできず、靭性等を劣化させることから、そ
の上限を0.015%とした。No matter what heat treatment is applied, P cannot completely eliminate its grain boundary segregation and deteriorates toughness, etc., so the upper limit of P is set to 0.015%.
SはMnと結合して割れの起点となり、さらに単独でも
粒界に偏析して脆化を促進するため、極力低く制限する
必要がある。従って、その上限を0.01%とした。S combines with Mn to become a starting point for cracks, and even when S is used alone, it segregates at grain boundaries and promotes embrittlement, so it is necessary to limit S to as low as possible. Therefore, the upper limit was set at 0.01%.
■は鋼を細粒化し、さらに析出硬化によって鋼の強度を
向上させる作用を有し、特にCr、 Mo、 Nbとの
複合添加でそれらの作用が顕著になる。 0.01%未
満では前記効果が得られず、0.30%を超えて含有さ
せると効果が飽和する上に却って靭性の劣化を招く場合
があることから、その含有量を0.01〜0.30%と
した。(2) has the effect of making the steel grain finer and further improving the strength of the steel through precipitation hardening, and these effects become particularly noticeable when combined with Cr, Mo, and Nb. If the content is less than 0.01%, the above effect cannot be obtained, and if the content exceeds 0.30%, the effect is saturated and the toughness may deteriorate. .30%.
Bは鋼の焼入性を一段と向上させる作用があるので、特
に成品寸法が大きい場合に高強度を確保する目的で添加
するが、その含有量が0.0003%未満では所望の効
果が得られず、また、0.0050%を超えて含有させ
ると靭性が劣化するようになることから、その含有量を
0.0003〜0.0050%とした。B has the effect of further improving the hardenability of steel, so it is added to ensure high strength especially when the dimensions of the product are large, but if the content is less than 0.0003%, the desired effect cannot be obtained. Furthermore, if the content exceeds 0.0050%, the toughness will deteriorate, so the content was set to 0.0003 to 0.0050%.
N1は綱の強度、靭性を向上させる効果があるが、0.
01%未満では前記効果が得られず、また、2.00%
を超えて含有させると効果が飽和する上、コストが高(
つくことから、その含有量を0.01〜2.00%とし
た。N1 has the effect of improving the strength and toughness of the rope, but 0.
If it is less than 0.01%, the above effect cannot be obtained, and if it is less than 2.00%
If it is contained in excess of
Therefore, the content was set to 0.01 to 2.00%.
(実施例) 以下、実施例に基づいて説明する。(Example) The following will explain based on examples.
通常の方法を用いて第1表に示す成分組成の綱(符号A
〜■)を溶製した。同表中の鋼A−Mは、本発明の範囲
内の組成を有するもので、鋼N〜■は*印を付した点に
おいてこの発明の範囲から外れた組成のものである。Using the usual method, the component composition shown in Table 1 (symbol A
~■) were melted. Steels A to M in the same table have compositions within the scope of the present invention, and steels N to ■ have compositions outside the scope of the present invention in the points marked with *.
上記した成分組成の@A−Vを連続鋳造法、あるいは鋼
塊法にて綱片とした後、1200〜1250“Cに加熱
して301厚さに熱間圧延し、その後、球状化焼鈍を施
したあと、表面を切削除去し、25−厚さとした。この
材料を冷間圧延にて7.51厚さ(圧下率70%)にし
た後、これを900°Cから焼入処理を施し、オーステ
ナイト結晶粒度試験を行った。After @A-V with the above-mentioned composition was made into a steel piece by continuous casting method or steel ingot method, it was heated to 1200 to 1250"C and hot rolled to a thickness of 301 mm, and then spheroidized annealed. After applying the material, the surface was cut and removed to give a thickness of 25 mm.This material was cold rolled to a thickness of 7.51 mm (reduction rate of 70%), and then quenched at 900°C. , an austenite grain size test was conducted.
γ粒粗大化の判定等、試験結果を第1表に併せ示す、な
お、第1表の粒度とはJIS GO551r鋼のオース
テナイト結晶粒度試験方法」に基づき測定した粒度であ
る。The test results, such as the determination of γ grain coarsening, are also shown in Table 1. The grain size in Table 1 is the grain size measured based on the JIS GO551r steel austenite grain size test method.
同表から明らかなように、本発明鋼A−Mにおいては、
1粒の粗大化は認められず、健全な組織を呈していた。As is clear from the table, in the steels A-M of the present invention,
No coarse grains were observed, indicating a healthy structure.
(以下、余白)
(発明の効果)
本発明の鋼は、冷間で強加工を加えた後の焼入れ時に発
生する1粒の粗大化がなく、靭性の劣化や熱処理歪のな
い優れた機械構造用鋼である。しかも、この鋼は低コス
トで製造することができ、工業上における実用価値は極
めて大きい。(Hereinafter, the margins) (Effects of the invention) The steel of the present invention has an excellent mechanical structure without the coarsening of a single grain that occurs during quenching after severe cold working, and without deterioration of toughness or heat treatment distortion. It is steel for industrial use. Moreover, this steel can be manufactured at low cost and has extremely high practical value in industry.
Claims (2)
20% Al:0.005〜0.10% N:0.035%以下 を含有し、かつ 1.00≦Al(%)/N(%)≦2.00 なる式を満足し、残部はFe及び不可避的不純物からな
り、不純物中のPは0.015%以下、Sは0.01%
以下であることを特徴とする冷間加工用鋼。(1) In weight%, C: 0.30-0.50% Si: 0.50% or less Mn: less than 0.50% Cr: 0.1-5.0% Mo: 0.01-0.80 % Hb: 0.005-0.
20% Al: 0.005 to 0.10% N: 0.035% or less, and satisfies the following formula: 1.00≦Al(%)/N(%)≦2.00, and the remainder is Fe. and unavoidable impurities, P in the impurities is 0.015% or less, S is 0.01%
A cold working steel characterized by:
050% Ni:0.01〜2.00% の1種以上を含有する請求項(1)記載の冷間加工用鋼
。(2) As component elements, further V: 0.01 to 0.30% B: 0.0003 to 0.0
050% Ni: The steel for cold working according to claim 1, containing one or more of 0.01% to 2.00% Ni.
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP4073689A JPH02217437A (en) | 1989-02-20 | 1989-02-20 | Steel for cold working |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP4073689A JPH02217437A (en) | 1989-02-20 | 1989-02-20 | Steel for cold working |
Publications (1)
Publication Number | Publication Date |
---|---|
JPH02217437A true JPH02217437A (en) | 1990-08-30 |
Family
ID=12588919
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
JP4073689A Pending JPH02217437A (en) | 1989-02-20 | 1989-02-20 | Steel for cold working |
Country Status (1)
Country | Link |
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JP (1) | JPH02217437A (en) |
Cited By (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH0551698A (en) * | 1991-03-26 | 1993-03-02 | Sumitomo Metal Ind Ltd | Steel for bolt and nut excellent in fire-resistance |
JP2009293095A (en) * | 2008-06-06 | 2009-12-17 | Sumitomo Metal Ind Ltd | High-strength steel for bolt |
-
1989
- 1989-02-20 JP JP4073689A patent/JPH02217437A/en active Pending
Cited By (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH0551698A (en) * | 1991-03-26 | 1993-03-02 | Sumitomo Metal Ind Ltd | Steel for bolt and nut excellent in fire-resistance |
JP2009293095A (en) * | 2008-06-06 | 2009-12-17 | Sumitomo Metal Ind Ltd | High-strength steel for bolt |
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