JPS6082618A - Production of steel bar wire rod having superior resistance to strain aging - Google Patents
Production of steel bar wire rod having superior resistance to strain agingInfo
- Publication number
- JPS6082618A JPS6082618A JP18862383A JP18862383A JPS6082618A JP S6082618 A JPS6082618 A JP S6082618A JP 18862383 A JP18862383 A JP 18862383A JP 18862383 A JP18862383 A JP 18862383A JP S6082618 A JPS6082618 A JP S6082618A
- Authority
- JP
- Japan
- Prior art keywords
- steel bar
- wire
- aging
- steel
- age hardening
- 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
Classifications
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/06—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires
Landscapes
- Engineering & Computer Science (AREA)
- Chemical & Material Sciences (AREA)
- Manufacturing & Machinery (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Heat Treatment Of Strip Materials And Filament Materials (AREA)
Abstract
Description
【発明の詳細な説明】
本発明は加工度の大きい特殊なボルト、ナツト、小ねじ
等の冷間鍛造用鋼に係シ、斐形抵抗を小さくして工具芽
命の延長を図ると共に、製品の靭性を改善したものであ
る。[Detailed Description of the Invention] The present invention relates to steel for cold forging such as special bolts, nuts, machine screws, etc. that require a large degree of processing. It has improved toughness.
近年冷間鍛造の分野においては、ボルトフォーマー、パ
ーツフォーマ−等の普及に伴ない各種形状の部品が冷間
鍛造によって製造されるようになった。In recent years, in the field of cold forging, with the spread of bolt formers, parts formers, etc., parts of various shapes have come to be manufactured by cold forging.
従って冷間鍛造に供されるブランクは、加工中に100
〜200℃程度壕で温度上昇し、青熱脆性の温度域で冷
間鍛造されるため、冷間鍛造中に時効硬化して、工具寿
命が著しく低下すると共に、冷間鍛造後の製品も脆化す
ることになる。Therefore, blanks subjected to cold forging have a
The temperature rises in the trench by ~200°C, and cold forging is performed in the temperature range of blue brittleness, so age hardening occurs during cold forging, significantly shortening tool life, and the product after cold forging also becomes brittle. It will become
本発明者は上記したボルトフォーマ−、パーツフォーマ
−等の如き加工度の亮い部品を冷a■鍜進しても、加工
中に時効硬化の発生を小さくした棒ル“i線材の開発を
目的とし、種々の実験ω■究を重ねた結果知見したもの
で、C0,45j6以下、5i035%以下、MU 0
120%−2,00光、Po、040%以下、30.0
25%以下、sOt、At、 o、o 30%〜0.0
90え、N60 ppm以下を含みかツsoムAl/N
15以上とし、残部pe、不可避的不純物からなる棒
鋼線イ2に、熱間圧延後、冷却途中又は冷却後200〜
×100が5%坊下となるようにしたことを特徴とする
もノテ、Sol、Al含有亦をo、o a OX’−0
,090%とじS○ムA4/N〉’15とすることでN
をAtNとして固定した後Cを冷却途中又は冷却後20
0〜500℃の時効処理により炭化物として析出させ固
定することによって、CSNによる時効硬化を抑止した
ものである。The present inventor has developed a rod "i-wire" that reduces the occurrence of age hardening during processing even when parts with a high degree of processing such as bolt formers and parts formers are cold-rolled. As a result of various experiments and investigations, C0,45j6 or less, 5i035% or less, MU 0
120% - 2,00 light, Po, 040% or less, 30.0
25% or less, sOt, At, o, o 30% to 0.0
Contains 90 ppm or less of N60 ppm or less Al/N
15 or more, and the balance is PE and unavoidable impurities.
×100 is characterized by 5% reduction.O, o a OX'-0
,090% binding S○mu A4/N>'15
After fixing as AtN, C is cooled for 20 minutes during or after cooling.
By precipitating and fixing carbides through aging treatment at 0 to 500°C, age hardening due to CSN is suppressed.
本発明鋼における成分系としては、圧延寸まで抜用的に
冷mJ鍛造が可能である線材の引張シ強さが90’fi
であることが要請され、この引張強さに見合う成分系を
前提として、C,Si、 Mn、 SoムAt。As for the composition system of the steel of the present invention, the tensile strength of the wire rod, which can be universally cold-forged to rolling size, is 90'fi.
C, Si, Mn, Som At.
Nの組成範囲をそれぞれ上記のように定めたものである
が、これらの限定理由は次の通シである。The composition ranges of N are determined as described above, and the reasons for these limitations are as follows.
C:Cは本発明鋼材では、C0,45%以上にすると圧
縮率75%で加工割れが生ずるので、上限を0.45%
とした。又下限につい、ではClが少ない程時効性がよ
くなるので、特に規定し々い。C: In the steel of the present invention, if C exceeds 0.45%, processing cracks will occur at a compression ratio of 75%, so the upper limit is set to 0.45%.
And so. Regarding the lower limit, it is particularly difficult to specify since the lower the Cl content, the better the aging properties.
Si : Si、は時効性には影響しないが、脱酸ある
いは強度調整用に添加される程度なので、上限値を0.
85Xとした。0.35%を超えて含有せしめると冷間
鍛造加工性が劣下するので好ましくない。Si: Si does not affect aging properties, but is added for deoxidation or strength adjustment, so the upper limit should be set at 0.
It was set to 85X. If the content exceeds 0.35%, cold forging workability deteriorates, which is not preferable.
Mn : Mnは5fttに基く熱atJ圧延時の割れ
防止及び棒wI線材の強度調整用に用いられるもので、
2.00ち′を超える必要性はなく、まだ下限としては
、Sによる割れ防止のため最低0.20%が必要である
。Mn: Mn is used to prevent cracking during hot ATJ rolling based on 5ftt and to adjust the strength of rod wI wire.
There is no need to exceed 2.00%, and the lower limit is still required to be at least 0.20% to prevent cracking due to S.
SoムA2 : SoムAAについては、0.030%
以下ではNの固定に不足であシ、また0090%を超え
ると介在物が多くなるのでo、o a o%〜0090
%の範囲に設定した。Som A2: 0.030% for Som AA
If it is below, it will not be enough to fix N, and if it exceeds 0090%, there will be a lot of inclusions, so o, o a o% ~ 0090
% range.
N:Nについてはsot、、 A11i1r(1)上限
が0.090%であるので、S○ムA/!、/N >
15よυしてNの上限を60 ppmとしだ。N: For N, sot,, A11i1r(1) Since the upper limit is 0.090%, S○mu A/! ,/N>
15, and set the upper limit of N to 60 ppm.
時効処理温度二時効処3!1j温度については、Cの拡
散が200 ’C以下では悪いだめ析出が充分に行われ
ず、反則に500tを超えるとCの固溶度が大きいため
やはシ析めが不充分となるので200〜500℃の温度
範囲とした。一方冷間鍜造中の温度は100〜200℃
で、棒鋼腺拐の「ノ“効処理?1情反よシも低いから、
冷間鍛造中に時効処理の効果が失われることはなく、し
かも本発明のごとき棒1;i(i線材に対する時効処理
は従来全く行われていない。Aging treatment temperature 2 Aging treatment 3!1j As for the temperature, if the diffusion of C is below 200'C, precipitation will not occur sufficiently, and if it exceeds 500t, the solid solubility of C will be large and precipitation will not occur. Since the temperature was insufficient, the temperature range was set at 200 to 500°C. On the other hand, the temperature during cold forging is 100 to 200℃.
So, what about the “no” effect treatment of the steel bar? 1. I'm low on love, so
The effect of the aging treatment is not lost during cold forging, and in addition, no aging treatment has been performed on the rod 1;i (i wire rod) of the present invention.
次に本発明の試験結果について説明する。Next, test results of the present invention will be explained.
不発明鋼の成分系に屈する006%C−0,05%5i
−0,30%Mn系の鋼材を用い、18IljIfニ夕
(間圧延し、圧延−1,まの試験材と、300℃×1七
の時効処理を施した試験材とのそれぞれをI7.6m$
に伸線加工し、時効硬化試験を行うため100 ’Cx
1Hr保持した試験片について、Sot、A4/Nと時
効硬化率との関係を調査した結果を第1図に示す。006%C-0,05%5i that yields to the composition system of uninvented steel
-0.30% Mn-based steel material was rolled for 18IljIf nights (I7.6m). $
100'Cx for wire drawing and age hardening test
FIG. 1 shows the results of investigating the relationship between Sot, A4/N, and age hardening rate for test pieces held for 1 hour.
第1図は\横軸にS○ムA1.(%)/ N etJを
とシ、縦軸に時効硬化率をとり、曲線(3)は時効処理
を施しだもの、曲線■)は時効処理なしのものを示し、
時効硬ただしT、S :伸線後時効処理した場合の引張
強さ。Figure 1 shows S○mu A1 on the horizontal axis. (%) / N etJ, the vertical axis shows the age hardening rate, curve (3) shows the one subjected to aging treatment, curve (■) shows the one without aging treatment,
Aging hardness T, S: Tensile strength when subjected to aging treatment after wire drawing.
T、S:伸線のままの引張強さ。T, S: Tensile strength as drawn.
第1図に明らかな如(SoムAtC’A/N(へ)を1
5以上にし、時効処理を施したものが助効硬化宰5光以
下(斜線で示す本発明範囲)となっていることが理解さ
れる。As shown in Figure 1 (SomAtC'A/N(to) is 1
5 or more and subjected to aging treatment, it is understood that the auxiliary hardening value is 5 light or less (the range of the present invention indicated by diagonal lines).
さらに第2図に、不発明鋼の成分系に属する鋼でSoム
A4/N値を度えた3種類の試験材を18IIIfにタ
ー間圧延後それぞれ時効処理温度を父えてlHrの時効
処理を施した後L7.611Mj;に伸線加工し、時効
硬化試験を行うため1001S X IHr保持した試
験片の試験結果について、時効処理温度と時効硬化率の
関係を示す。図中曲線(イ)、(ロ)は0.06%C−
〇、05%Si −0,80%j鼎系銅系鋼線(ハ)は
0.23%C−0,25%Si、 −1,50%Mn系
鋼で、曲線(イ)はsoz、A4/N= 12.8、曲
線(ロ)はSOムA4/N = 31.4、曲線(ハ)
はSOt、At/N = 20.8で、横軸に線材の時
効処理温度を、縦軸に時効硬化率を示し、2点鎖線の範
囲が本発明の時効処理温度範囲を示す。なお時効硬化率
の算式は第1図の場合に同じである。Furthermore, Fig. 2 shows that three types of test materials, which are steels belonging to the compositional system of uninvented steels and have a high Som A4/N value, were rolled between 18IIIf and then aged for 1Hr at different aging temperatures. The relationship between the aging treatment temperature and the age hardening rate is shown for the test results of the test piece which was then wire drawn to L7.611Mj and held at 1001S x IHr for the age hardening test. Curves (a) and (b) in the figure are 0.06%C-
〇, 05%Si -0,80%j Ding-based copper steel wire (c) is 0.23%C-0,25%Si, -1,50%Mn-based steel, and the curve (a) is soz, A4/N = 12.8, curve (b) is SOmu A4/N = 31.4, curve (c)
is SOt, At/N = 20.8, the horizontal axis shows the aging temperature of the wire, the vertical axis shows the age hardening rate, and the range of the two-dot chain line shows the aging temperature range of the present invention. Note that the formula for the age hardening rate is the same as in the case of FIG.
第2図の結果から理解されるようにSOt、A4//N
が15以上の場合200〜500tでの時効処理によっ
てすぐれた時効硬化率が得られている。As understood from the results in Figure 2, SOt, A4//N
When is 15 or more, an excellent age hardening rate is obtained by aging treatment at 200 to 500 tons.
上記第1図、第2図の試験結果に基いて製作した不発明
鋼と比較鋼として示す従来鋼との比較を第1表に示す。Table 1 shows a comparison between the uninvented steel manufactured based on the test results shown in FIGS. 1 and 2 above and the conventional steel shown as comparative steel.
第1表の「判定」欄の○印は本発明が目的とするI+、
1j効硬化率5%以下であることを示し、X印は5%を
超えるものである。The ○ mark in the “Judgment” column of Table 1 indicates I+, which is the objective of the present invention.
1j indicates that the effective hardening rate is 5% or less, and the mark X indicates that it exceeds 5%.
第1表の実施例に明らかなように、本発明になる棒れ1
1線材は何れも所望する時効硬化率が得られているが、
比較鋼においては本発明の所望する時効硬化率が得られ
ず、従って比較鋼にあっては本願が企図する製品の冷間
鍛造中に発生する歪時効の抑止効果は期待し得ない。As is clear from the examples in Table 1, the rod 1 according to the present invention
Although the desired age hardening rate was obtained for each of the 1 wire rods,
The age hardening rate desired by the present invention cannot be obtained in the comparative steel, and therefore, the comparative steel cannot be expected to have the effect of suppressing strain aging that occurs during cold forging of products as contemplated by the present invention.
以上に詳細説明した如く、本iし明は加工度の大きい特
殊なボルト、ナツト、小ねじ等の冷間鍛造部品用の1i
71 Uとして、変形抵抗を小さくし、工具寿命の延長
を図ると共に、υψ品の靭性を大巾に改辞するという多
大の効果を有する棒鋼線材の製造を可能にしたものであ
る。As explained in detail above, this book is a 1i for cold forged parts such as special bolts, nuts, machine screws, etc. that require a large degree of machining.
71U, it has made it possible to manufacture a steel bar wire rod that has the great effect of reducing deformation resistance, extending tool life, and significantly improving the toughness of υψ products.
第1図はSOl、Al/Nと時効硬化率との関係を示す
曲線図、第2図は、線材の時効処理温度と時効硬化率と
の関係を示す曲線図である・
第 1 図
曙
5°2°Ae(%yN(%)
第2図
線羽/)脚効処理温皮(°C)Figure 1 is a curve diagram showing the relationship between SOI, Al/N and age hardening rate, and Figure 2 is a curve diagram showing the relationship between aging treatment temperature of wire and age hardening rate. °2°Ae (%yN (%) Figure 2 Line Feather/) Leg effect treatment warm skin (°C)
Claims (1)
下、Mn 0.20%−2,00%、P O,040%
以下、30.025%以下、Sol、Al O,030
%−0,090%、N 60 I)9m以下を含みかつ
5oi−A4/N15以上で、残部Feおよび不可避的
不純物がら々る棒鋼線材に、熱間圧延後、玲却途中又は
冷却後200〜500℃の11.5効処理を施し、下記
算式による11計幼硬化率が5%以下となるようにした
ことを特徴とする1ω1歪民ただし T、S 二仲線後
時効処理した場合の引張強さ。 T、S :伸線の捷まの引張強さ。(1) CO, 45XDIT, Si O, 85XJ”J
Bottom, Mn 0.20%-2,00%, PO, 040%
Below, 30.025% or less, Sol, Al O, 030
%-0,090%, N 60 I) 9m or less, 5oi-A4/N15 or more, the balance Fe and a lot of inevitable impurities, after hot rolling, during cooling or after cooling 200 ~ A 1ω1 strained material characterized by being subjected to 11.5-effect treatment at 500°C and having an 11-total infant hardening rate of 5% or less according to the following formula. strength. T, S: Tensile strength of wire drawing.
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP18862383A JPS6082618A (en) | 1983-10-08 | 1983-10-08 | Production of steel bar wire rod having superior resistance to strain aging |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP18862383A JPS6082618A (en) | 1983-10-08 | 1983-10-08 | Production of steel bar wire rod having superior resistance to strain aging |
Publications (1)
Publication Number | Publication Date |
---|---|
JPS6082618A true JPS6082618A (en) | 1985-05-10 |
Family
ID=16226921
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
JP18862383A Pending JPS6082618A (en) | 1983-10-08 | 1983-10-08 | Production of steel bar wire rod having superior resistance to strain aging |
Country Status (1)
Country | Link |
---|---|
JP (1) | JPS6082618A (en) |
Cited By (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
EP1939309A1 (en) | 2006-12-28 | 2008-07-02 | Kabushiki Kaisha Kobe Seiko Sho | Steel for high-speed cold working and method for production thereof, and part formed by high-speed cold working and method for production thereof |
Citations (4)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS5760416A (en) * | 1980-09-30 | 1982-04-12 | Kanbishi Denki Seizo Kk | Control device for gas burning output proportion |
JPS5822333A (en) * | 1981-08-03 | 1983-02-09 | Nippon Kokan Kk <Nkk> | Production of high-strength cold-rolled steel sheet excellent in press-formability and baking-hardenability |
JPS5848632A (en) * | 1981-09-18 | 1983-03-22 | Nippon Kokan Kk <Nkk> | Production of mild cold rolled steel plate for drawing having excellent aging resistance by continuous annealing |
JPS5848637A (en) * | 1981-09-18 | 1983-03-22 | Nippon Steel Corp | Manufacture of cold rolled steel plate with superior press formability |
-
1983
- 1983-10-08 JP JP18862383A patent/JPS6082618A/en active Pending
Patent Citations (4)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS5760416A (en) * | 1980-09-30 | 1982-04-12 | Kanbishi Denki Seizo Kk | Control device for gas burning output proportion |
JPS5822333A (en) * | 1981-08-03 | 1983-02-09 | Nippon Kokan Kk <Nkk> | Production of high-strength cold-rolled steel sheet excellent in press-formability and baking-hardenability |
JPS5848632A (en) * | 1981-09-18 | 1983-03-22 | Nippon Kokan Kk <Nkk> | Production of mild cold rolled steel plate for drawing having excellent aging resistance by continuous annealing |
JPS5848637A (en) * | 1981-09-18 | 1983-03-22 | Nippon Steel Corp | Manufacture of cold rolled steel plate with superior press formability |
Cited By (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
EP1939309A1 (en) | 2006-12-28 | 2008-07-02 | Kabushiki Kaisha Kobe Seiko Sho | Steel for high-speed cold working and method for production thereof, and part formed by high-speed cold working and method for production thereof |
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