JPS61130424A - Production of heat treatment-omission type high tension steel wire or rod having excellent workability - Google Patents
Production of heat treatment-omission type high tension steel wire or rod having excellent workabilityInfo
- Publication number
- JPS61130424A JPS61130424A JP25298584A JP25298584A JPS61130424A JP S61130424 A JPS61130424 A JP S61130424A JP 25298584 A JP25298584 A JP 25298584A JP 25298584 A JP25298584 A JP 25298584A JP S61130424 A JPS61130424 A JP S61130424A
- Authority
- JP
- Japan
- Prior art keywords
- less
- steel
- temperature range
- heat treatment
- excellent workability
- 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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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
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/52—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length
- C21D9/525—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length for wire, for rods
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (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、引張強さ６０ ｋｇｆ／ａｖ＋”以上、絞り
５０％以上である加工性のすぐれた熱処理省略型高張力
線材棒鋼の製造方法に関する。DETAILED DESCRIPTION OF THE INVENTION The present invention relates to a method for manufacturing a high-strength wire rod steel bar that has a tensile strength of 60 kgf/av+'' or more, a reduction of area of 50% or more, and has excellent workability and does not require heat treatment.
従来、引張強さ６０ｋｇｆ／ｍｎ＋”以上のボルトや小
ねじのファスナ一部品には、Ｃが０．３０重量％以上の
中高炭素鋼或いは低合金鋼が用いられており、これら部
品は通常、球状焼鈍し処理、冷間伸線、冷間ボルト成形
、焼入れ及び焼戻しの工程を経て製造されている。また
、チェーン用リンクプレート等の部品も帯鋼を冷間打抜
き加工し、焼入れ、焼戻しの工程を経て製造されている
。しかし、近年、省エネルギーに対する要請の高まりを
１景として、球状焼鈍し処理や焼入れ焼戻し処理を省略
し得て、しかも、加工性にすぐれた高張力線材棒鋼が要
望されている。Conventionally, fastener parts for bolts and machine screws with a tensile strength of 60 kgf/mn+" or more have been made of medium-high carbon steel or low alloy steel with a C content of 0.30% by weight or more, and these parts are usually spherical. It is manufactured through the processes of annealing, cold wire drawing, cold bolt forming, quenching and tempering.Parts such as chain link plates are also manufactured by cold punching the steel strip, followed by quenching and tempering. However, in recent years, with the increasing demand for energy conservation, there has been a demand for high-tensile wire rod steel bars that can omit the spherical annealing process and quenching and tempering processes and have excellent workability. There is.
本発明者らは、かかる要望に応えるべく鋭意研究した結
果、既に、低炭素低合金鋼を所定の条件にて熱間加工し
た後、急冷することにより、鋼組織をフェライト・マル
テンサイト複合組織となし、かくして、加工性のすぐれ
た熱処理省略型高張力線材棒鋼を得ることができること
を見出している（特公昭５Ｂ−１０４４２号公報）。As a result of intensive research in response to such demands, the present inventors have already hot-worked low-carbon, low-alloy steel under predetermined conditions and then rapidly cooled it to transform the steel structure into a ferrite-martensitic composite structure. In this way, it has been discovered that it is possible to obtain a heat-treated high-strength wire rod with excellent workability (Japanese Patent Publication No. 5B-10442).
しかし、上記のようにして得られた複合組織を有する高
張力線材棒鋼においても、特に、加工性が厳しい用途、
例えば、高張力ボルトやリンクプレート等の製造時に尚
、割れの生じる傾向があることが見出された。そこで、
本発明者らは、かかる割れの生じる原因について更に研
究を重ねた結果、この割れが線材棒鋼における靭性低下
と関連しており、従って、所定の化学成分を有する低炭
素低合金鋼を熱間加工した後、所定の温度範囲まで冷却
して、鋼組織をフェライトと低温変態生成相との複合組
織となすと共に、得られた線材棒鋼を所定の温度範囲に
再加熱して、その靭性を改善することにより、球状化焼
鈍し処理や焼入れ焼戻し処理を省略することを可能とし
た、高張力ボルト等の加工性の厳しい製品の製造時の割
れを防止することができる線材棒鋼を得ることができる
ことを見出して、本発明に至ったものである。However, even in the high-tensile wire rod steel bar having a composite structure obtained as described above, it is difficult to use the
For example, it has been found that there is still a tendency for cracking to occur during the manufacture of high tensile strength bolts, link plates, and the like. Therefore,
As a result of further research into the causes of such cracks, the present inventors discovered that this cracking is associated with a decrease in toughness in wire rod steel bars. After that, it is cooled to a predetermined temperature range to make the steel structure a composite structure of ferrite and a phase formed by low-temperature transformation, and the obtained wire rod steel bar is reheated to a predetermined temperature range to improve its toughness. By doing this, it is possible to obtain a wire rod that can omit spheroidizing annealing treatment and quenching and tempering treatment, and can prevent cracking during the production of products that are difficult to work with, such as high-tensile bolts. This discovery led to the present invention.
従って、本発明は、特に、ボルト等の加工性の厳しい用
途に好適に使用することができる加工性のすぐれた熱処
理省略型高張力線材棒鋼の製造方法を提供することを目
的とする。Therefore, an object of the present invention is to provide a method for manufacturing a high-tensile steel wire bar without heat treatment, which has excellent workability and can be particularly suitably used in applications requiring severe workability, such as bolts.
本発明による加工性のすぐれた熱処理省略型高張力線材
棒鋼の製造方法は、重量％で
ｃ ｏ、ｏｓ〜０．２０％、
Ｓｉ１．０％以下、及び
Ｍｎ １．０〜２．５％
を含有する綱を熱間加工した後、８００〜９５０℃の温
度範囲から平均冷却速度１〜ｂ
て２００℃未満の温度範囲まで冷却して、体積含有率４
０〜７５％のフェライトと残部がマルテンサイト、ベイ
ナイト又はこれらの混合組織からなる低温変態生成相と
の複合組織となし、次いで、２００〜６００℃の温度範
囲に加熱することを特徴とする。The method for manufacturing a high-strength wire rod steel bar without heat treatment with excellent workability according to the present invention includes CO, OS ~ 0.20%, Si 1.0% or less, and Mn 1.0-2.5% in weight percent. After hot working the contained steel, it is cooled from a temperature range of 800 to 950 °C to a temperature range of less than 200 °C at an average cooling rate of 1 to b, and the volume content is 4.
It is characterized by forming a composite structure of 0 to 75% ferrite and a low-temperature transformation phase with the remainder consisting of martensite, bainite, or a mixed structure thereof, and then heating to a temperature range of 200 to 600°C.
先ず、本発明による鋼における成分元素の限定理由につ
いて説明する。First, the reasons for limiting the constituent elements in the steel according to the present invention will be explained.
Ｃは、固溶強化によって綱に所要の強度を与えるために
必要であり、本発明鋼においては少なくとも０．０５％
の添加を必要とする。しかし、過多に添加するときは、
鋼の変形抵抗を高め、特に、０．２０％を越えるときは
鋼の加工性が著しく増大するので、Ｃの含有量の上限を
０．２０％とする。C is necessary to give the steel the required strength through solid solution strengthening, and in the steel of the present invention, it is at least 0.05%.
Requires the addition of However, when adding too much,
C increases the deformation resistance of the steel, and in particular, when it exceeds 0.20%, the workability of the steel increases significantly, so the upper limit of the C content is set at 0.20%.
Ｓｉは、Ｃと同様に固溶強化によって鋼の強度を高める
効果が大きいが、過多に添加するときは、著しい靭性劣
化をもたらし、更に、脱炭をも著しく増大させるので、
添加量の上限を１．０％とする。Like C, Si has a great effect of increasing the strength of steel through solid solution strengthening, but when added in excess, it causes a significant deterioration of toughness and also significantly increases decarburization.
The upper limit of the amount added is 1.0%.
Ｍｎは、鋼の強靭化と熱間加工後の冷却に際して所望の
組織を得るために添加されるが、添加量が１．０％より
も少ないときは、上記効果を十分に得ることができず、
一方、２．５％を越えるときは、製造時にＭｎの偏析増
大に伴って加工性が低下する。従って、Ｍｎの添加量は
１．０〜２．５％の範囲とする。Mn is added to strengthen the steel and obtain a desired structure during cooling after hot working, but when the amount added is less than 1.0%, the above effects cannot be sufficiently obtained. ,
On the other hand, when it exceeds 2.5%, workability decreases due to increased segregation of Mn during manufacturing. Therefore, the amount of Mn added is in the range of 1.0 to 2.5%.
本発明による高張力線材棒鋼の製造方法においては、上
記のような化学組成を有する鋼を加熱し、先ず、線材棒
鋼への通常の熱間加工を施す。本発明においては、鋼加
熱温度に特に制限されないが、好ましくは９００〜１１
００℃の範囲である。加熱温度が１１００℃を越えると
きは、結晶粒の粗大化や脱炭が生じることがあり、一方
、９００℃よりも低いときは、熱間圧延において鋼の変
形抵抗が増大し、得られる線材棒鋼に表面疵が発生する
ことがあるからである。In the method for manufacturing a high-tensile steel wire rod according to the present invention, steel having the above chemical composition is heated and first subjected to normal hot working into a wire rod. In the present invention, the steel heating temperature is not particularly limited, but preferably 900 to 11
It is in the range of 00°C. When the heating temperature exceeds 1100°C, coarsening of grains and decarburization may occur, while when the heating temperature is lower than 900°C, the deformation resistance of the steel increases during hot rolling, and the resulting wire rod steel bar This is because surface flaws may occur on the surface.
本発明においては、このように加熱した鯛を熱間圧延す
るが、圧延仕上温度は８５０〜１２００℃の範囲とし、
好ましくは９００〜１１５０℃の範囲である。圧延仕上
温度が１２００℃を越える高温であるときは、結晶粒が
粗大化するので、例えば、得られた線材棒鋼をボルト成
形する際の加工性が劣化し、また、得られるボルトも特
性に劣ることとなる。他方、圧延仕上温度は、結晶粒の
挙動からみれば、低温度であるほど、結晶粒が細かくな
り、綱の靭性が向上するが、反面、生産性の低下が著し
いので、本発明においては、圧延仕上温度は、８５０℃
以上とする。In the present invention, the sea bream heated in this way is hot rolled, and the rolling finishing temperature is in the range of 850 to 1200°C,
Preferably it is in the range of 900 to 1150°C. When the rolling finishing temperature is a high temperature exceeding 1200°C, the crystal grains become coarse, so for example, the workability when forming the obtained wire rod into a bolt deteriorates, and the obtained bolt also has poor properties. That will happen. On the other hand, in terms of the behavior of crystal grains, the lower the rolling finishing temperature, the finer the crystal grains and the better the toughness of the steel, but on the other hand, the productivity is significantly lowered. Rolling finishing temperature is 850℃
The above shall apply.
上記の熱間圧延後の冷却開始温度を８００〜９５０℃の
温度範囲とし、この温度範囲から平均冷却速度１〜ｂ
囲まで冷却する。冷却開始温度が９５０℃を越える高温
であるときは、フェライト析出量の調整が困難であり、
所定の組織を得ることができない。The cooling start temperature after the above-mentioned hot rolling is set in a temperature range of 800 to 950°C, and cooling is performed from this temperature range to an average cooling rate of 1 to b. When the cooling start temperature is a high temperature exceeding 950°C, it is difficult to adjust the amount of ferrite precipitation.
It is not possible to obtain a given tissue.
一方、冷却開始温度が８００℃よりも低いときも、フェ
ライト析出量の調整が困難であり、得られる製品の品質
を一定に保つことが困難となる。On the other hand, when the cooling start temperature is lower than 800° C., it is also difficult to adjust the amount of ferrite precipitation, making it difficult to maintain the quality of the obtained product constant.
次いで、上記冷却開始温度から平均冷却速度１〜ｂ
却することにより、得られる鋼ｍ織を体積含有率４０〜
７５％のフェライトと残部がマルテンサイト、ベイナイ
ト又はこれらの混合組織からなる低温変態生成相との複
合組織とする。冷却速度が１℃／秒よりも遅いときは、
フェライト相の析出に引き続いてパーライト相が析出す
ることがあるので好ましくなく、他方、１５℃／秒を越
えるときは、所要のフェライト体積含有率を有する複合
組織を得ることが困難となり、この結果、強度及び靭性
のばらつきが大きくなる傾向が高まる。従って、本発明
の方法においては、平均冷却速度を１〜ｂ
本発明においては、圧延線材棒鋼を上記のように所定の
平均冷却速度によって２００℃未満の温度範囲まで冷却
した後、２００〜６００℃の温度範囲に再加熱すること
によって高靭性化を図る。Next, by cooling the average cooling rate from the above cooling start temperature to 1~b, the obtained steel m weave has a volume content of 40~
It has a composite structure consisting of 75% ferrite and the remainder consisting of martensite, bainite, or a mixed structure thereof with a phase produced by low-temperature transformation. When the cooling rate is slower than 1℃/sec,
This is not preferable because the pearlite phase may precipitate following the precipitation of the ferrite phase. On the other hand, when the temperature exceeds 15°C/sec, it becomes difficult to obtain a composite structure having the required ferrite volume content, and as a result, The tendency for greater variation in strength and toughness increases. Therefore, in the method of the present invention, the average cooling rate is 1 to b.In the present invention, after cooling the rolled wire rod to a temperature range of less than 200°C at a predetermined average cooling rate as described above, Toughness can be increased by reheating to a temperature range of .
従来の焼入れ焼戻し処理されるボルト等については、こ
の熱処理の調整によって強度のばらつきを抑えることが
でき、例えば、ＪＩＳ Ｂ １０５１及びＩＳｏ ８９
８／１に規定されている強度範囲（約２０ｋｇｆ／＋ｗ
ｍ” ）よりかなり狭い範囲（約５ｋｇｆ／ｍｍ” ）
に調整されている。本発明によれば、冷却停止温度が２
００℃を越える温度であっても、上記規格を満足するこ
とはできるが、強度のばらつきを一層小さくして、製品
品質の向上を図るために冷却停止温度を２００℃未満と
する。For bolts and the like that are conventionally quenched and tempered, variations in strength can be suppressed by adjusting this heat treatment. For example, JIS B 1051 and ISO 89
Strength range specified in 8/1 (approximately 20 kgf/+w
m”) much narrower range (approximately 5kgf/mm”)
has been adjusted to. According to the present invention, the cooling stop temperature is 2
Although the above specifications can be satisfied even at temperatures exceeding 00°C, the cooling stop temperature is set to less than 200°C in order to further reduce variations in strength and improve product quality.
しかし、このように冷却停止温度を２００″Ｃ未満とす
るとき、低温変態生成相中のＣａ１度が高くなり、靭性
が劣化する。ここで、再加熱温度もまた２００℃未満と
すれば、所要の靭性を得るためには、実操業上、不適当
にすぎる長時間を要することとなり、一方、６００℃を
越えるときは、低温変態生成相の焼戻しが過剰になるの
で、所要の強度を得ることが困難となる。好ましくは、
再加熱温度は３００〜５５０℃の範囲である。特に好ま
しい再加熱温度の上限は約５００℃である。However, when the cooling stop temperature is set to less than 200"C, the Ca1 degree in the low-temperature transformation product phase increases and the toughness deteriorates. Here, if the reheating temperature is also set to less than 200"C, the required In order to obtain this toughness, it would take an unsuitable long time in actual operation. On the other hand, when the temperature exceeds 600°C, the tempering of the low-temperature transformation phase becomes excessive, so it is difficult to obtain the required strength. is difficult. Preferably,
Reheating temperature ranges from 300 to 550°C. A particularly preferred upper limit of the reheating temperature is about 500°C.
本発明によれば、最終的に得られる鋼組織を体積含有率
４０〜７５％のフェライトと残部がマルテンサイト、ベ
イナイト又はこれらの混合組織からなる低温変態生成相
との複合組織とする。フェライト体積含有率が４０〜７
５％の範囲外にあるとき、強度及び靭性のばらつきが大
きくなる。According to the present invention, the finally obtained steel structure is a composite structure of a low-temperature transformation-generated phase consisting of ferrite with a volume content of 40 to 75% and the remainder consisting of martensite, bainite, or a mixed structure thereof. Ferrite volume content is 40-7
When it is outside the range of 5%, variations in strength and toughness become large.
このようにして得られる線材棒鋼は、靭性が著しく改善
され、従って、高張力ボルトのような厳しい冷間加工性
が要求される用途においても、割れの発生を防止するこ
とができる。The wire rod obtained in this way has significantly improved toughness, and therefore can prevent cracking even in applications that require severe cold workability, such as high-tensile bolts.
更に、本発明においては、線材棒鋼の強靭化及び自己焼
戻しによる軟化抵抗の増大を図り、強度のばらつきを減
少させるために、
Ｃｒ １．０％以下、及び
ＭＯｏ、３％以下
よりなる群から選ばれる少なくとも１種の元素を添加す
ることができる。Furthermore, in the present invention, in order to strengthen the wire rod steel bar and increase its softening resistance through self-tempering, and to reduce variations in strength, At least one element can be added.
また、結晶粒微細化及び固溶Ｎの低減による靭性の向上
等を図るために、
Ａβ ０．１％以下、
Ｎｂ０．１％以下、
Ｔｉ０．１％以下、及び
Ｚｒ０．３％以下
よりなる群から選ばれる少なくとも１種の元素を添加す
ることができる。In addition, in order to improve toughness by refining grains and reducing solid solution N, a group consisting of Aβ 0.1% or less, Nb 0.1% or less, Ti 0.1% or less, and Zr 0.3% or less At least one element selected from the following can be added.
また、介在物の形状を制御し、加工性を増大するために
、
ＲＥＭ ０．０５％以下、及び
Ｃａ ０．００３％以下
よりなる群から選ばれる少なくとも１種の元素を添加す
ることもでき、更に、靭性を一層向上させるために、Ｎ
ｔを１．０％以下の範囲で添加することもできる。Furthermore, in order to control the shape of inclusions and increase workability, at least one element selected from the group consisting of REM 0.05% or less and Ca 0.003% or less may be added, Furthermore, in order to further improve the toughness, N
It is also possible to add t in a range of 1.0% or less.
以上のようにして、本発明の方法により得られる線材棒
鋼は、靭性が改善される結果、冷間加工性にすぐれ、従
って、例えば、高張力ボルトの製造については、線材に
軽度の伸線加工を施した後、ねじ転造を含む冷間ボルト
成形によって、所要の特性を有するボルトを得ることが
できるので、球状化焼鈍し処理を省略することができる
。また、チェーン用リンクプレートの場合も、冷間平圧
加工を施し、冷間打抜き加工によって所要の特性を得る
ことができ、従って、焼入れ焼戻し処理を省略すること
ができる。As described above, the wire rod steel bar obtained by the method of the present invention has improved toughness and has excellent cold workability. After that, a bolt having the desired characteristics can be obtained by cold bolt forming including thread rolling, so that the spheroidizing annealing process can be omitted. Also, in the case of a link plate for a chain, the required properties can be obtained by performing cold flat pressure processing and cold punching, and therefore, the quenching and tempering process can be omitted.
尚、本発明において用いる鋼は、例えばＬＤ転炉にて溶
製されるが、溶製方法は何ら制限されるものではない。The steel used in the present invention is melted, for example, in an LD converter, but the melting method is not limited at all.
以下に実施例を比較例と共に挙げて本発明をより具体的
に説゛明する。EXAMPLES The present invention will be described in more detail below with reference to Examples and Comparative Examples.
実施例１
第１表に示す化学組成を有する鋼をＬＤ転炉で溶製し、
１０５０℃に加熱した後、径１０．３ ａｍ線材に圧延
仕上温度１１００℃にて熱間圧延し、この後、第１表に
示す条件にて冷却し、本発明の方法によるときは、これ
を第１表に示す温度に再加熱し、このようにして、本発
明線材及び比較線材をそれぞれ得た。尚、比較鋼として
は、再加熱条件が本発明で規定する範囲外とするものも
併せて示す。これら線材の機械的性質及び金属組織を第
１表に示す。本発明による線材は低炭素鋼であるにもか
かわらず、強度は６０ ｋｇｆ／ｍａｄ”以上、絞り値
も５０％以上であって、比較法による線材に比べて強度
−延性バランスにすぐれていることが明らかである。Example 1 Steel having the chemical composition shown in Table 1 was melted in an LD converter,
After heating to 1050°C, the wire rod with a diameter of 10.3 am is hot rolled at a finishing temperature of 1100°C, and then cooled under the conditions shown in Table 1. The wire rods were reheated to the temperatures shown in Table 1, and thus wire rods of the present invention and comparative wire rods were obtained. As comparative steels, steels whose reheating conditions are outside the range defined by the present invention are also shown. Table 1 shows the mechanical properties and metallographic structures of these wires. Although the wire rod according to the present invention is made of low carbon steel, it has a strength of 60 kgf/mad" or more and a reduction of area of 50% or more, and has a better balance of strength and ductility than wire rods made by comparative methods. is clear.
また、第１表における本発明鋼１．２．３及び４、澗Ａ
及びＣを再加熱しないもの（第２表１′及び３゛）、及
び比較１１９及び１６の圧延線材（径１０．３ｍ）をそ
れぞれ径９．０５ ｔａに伸線加工した。In addition, the present invention steels 1.2.3 and 4 in Table 1,
and C without reheating (Table 2, 1' and 3'), and the rolled wire rods of Comparisons 119 and 16 (diameter 10.3 m) were each drawn to a diameter of 9.05 ta.
これら鋼線の機械的性質、冷間圧縮試験結果及び冷間平
圧試験結果を第２表に示す。本発明の方法による鋼線は
、冷間圧縮加工性及び冷間平圧加工性にすぐれることが
明らかである。Table 2 shows the mechanical properties, cold compression test results, and cold flat pressure test results of these steel wires. It is clear that the steel wire produced by the method of the present invention has excellent cold compression workability and cold flat pressure workability.
実施例２
第１表に示す本発明鋼Ａ、Ｂ、Ｃ及びＤを所定のねし呼
び径になるように圧延及び冷間伸線加工を行ない、その
後、六角ボルトに圧造した。圧延結果及びボルト性能を
第３表に示す。尚、片振り疲労試験は平均応力４０ ｋ
ｇｆ／＋ｍｍｔにて１０１回の繰返し数まで試験した。Example 2 Invention steels A, B, C, and D shown in Table 1 were rolled and cold wire-drawn to a predetermined nominal diameter, and then pressed into hexagonal bolts. Table 3 shows the rolling results and bolt performance. In addition, the average stress of the oscillation fatigue test was 40 k.
Tested up to 101 repetitions at gf/+mmt.
従来、ＪＩＳ Ｂ １０５１及びＩＳＯ８９Ｂ／１に規
定されている強度区分８．８級及び９．８級のボルトは
主に焼入れ焼戻し処理されているが、本発明鋼によれば
、第３表に示すように、焼入れ焼戻し処理を要せずして
、上記規格を満足する。また、従来のボルトと比較して
同等又はそれ以上の性能を有する。Conventionally, bolts with strength classes 8.8 and 9.8 specified in JIS B 1051 and ISO 89B/1 have been mainly quenched and tempered, but according to the steel of the present invention, the bolts shown in Table 3 As such, it satisfies the above standards without requiring quenching and tempering treatment. It also has performance equivalent to or better than conventional bolts.
Claims (5)
度範囲から平均冷却速度１〜１５℃／秒にて２００℃未
満の温度範囲まで冷却して、体積含有率４０〜７５％の
フェライトと残部がマルテンサイト、ベイナイト又はこ
れらの混合組織からなる低温変態生成相との複合組織と
なし、次いで、２００〜６００℃の温度範囲に加熱する
ことを特徴とする加工性のすぐれた熱処理省略型高張力
線材棒鋼の製造方法。(1) After hot working steel containing 0.05 to 0.20% C, 1.0% or less Si, and 1.0 to 2.5% Mn by weight, the temperature range is 800 to 950°C. to a temperature range below 200°C at an average cooling rate of 1 to 15°C/sec to produce a low-temperature transformation phase consisting of ferrite with a volume content of 40 to 75% and the remainder martensite, bainite, or a mixed structure thereof. A method for producing a heat treatment-free high-tensile wire steel bar with excellent workability, the method comprising forming a composite structure with a composite structure of the steel bar and heating it to a temperature range of 200 to 600°C.
度範囲から平均冷却速度１〜１５℃／秒にて２００℃未
満の温度範囲まで冷却して、体積含有率４０〜７５％の
フェライトと残部がマルテンサイト、ベイナイト又はこ
れらの混合組織からなる低温変態生成相との複合組織と
なし、次いで、２００〜６００℃の温度範囲に加熱する
ことを特徴とする加工性のすぐれた熱処理省略型高張力
線材棒鋼の製造方法。(2) In addition to (a) C 0.05 to 0.20%, Si 1.0% or less, and Mn 1.0 to 2.5% by weight, (b) Cr 1.0% or less, After hot working steel containing at least one element selected from the group consisting of 0.3% or less of Mo, the steel is heated to 200°C at an average cooling rate of 1 to 15°C/sec from a temperature range of 800 to 950°C. It is then cooled to a temperature range of 200 to 600°C to form a composite structure of ferrite with a volume content of 40 to 75% and a low-temperature transformation phase with the remainder consisting of martensite, bainite, or a mixed structure of these. A method for producing a high-tensile steel wire bar with excellent workability that does not require heat treatment and is characterized by heating to a temperature range.
度範囲から平均冷却速度１〜１５℃／秒にて２００℃未
満の温度範囲まで冷却して、体積含有率４０〜７５％の
フェライトと残部がマルテンサイト、ベイナイト又はこ
れらの混合組織からなる低温変態生成相との複合組織と
なし、次いで、２００〜６００℃の温度範囲に加熱する
ことを特徴とする加工性のすぐれた熱処理省略型高張力
線材棒鋼の製造方法。(3) In addition to (a) C 0.05-0.20%, Si 1.0% or less, and Mn 1.0-2.5% in weight%, (b) Al 0.1% or less, After hot working steel containing at least one element selected from the group consisting of Nb 0.1% or less, Ti 0.1% or less, and Zr 0.3% or less, a temperature range of 800 to 950 ° C. to a temperature range below 200°C at an average cooling rate of 1 to 15°C/sec to produce a low-temperature transformation phase consisting of ferrite with a volume content of 40 to 75% and the remainder martensite, bainite, or a mixed structure thereof. A method for producing a heat treatment-free high-tensile wire steel bar with excellent workability, the method comprising forming a composite structure with a composite structure of the steel bar and heating it to a temperature range of 200 to 600°C.
度範囲から平均冷却速度１〜１５℃／秒にて２００℃未
満の温度範囲まで冷却して、体積含有率４０〜７５％の
フェライトと残部がマルテンサイト、ベイナイト又はこ
れらの混合組織からなる低温変態生成相との複合組織と
なし、次いで、２００〜６００℃の温度範囲に加熱する
ことを特徴とする加工性のすぐれた熱処理省略型高張力
線材棒鋼の製造方法。(4) In addition to (a) C 0.05-0.20%, Si 1.0% or less, Mn 1.0-2.5%, (b) REM 0.05% or less, and After hot working steel containing at least one element selected from the group consisting of Ca 0.003% or less, from a temperature range of 800 to 950°C to less than 200°C at an average cooling rate of 1 to 15°C/sec. It is cooled to a temperature range of 200 to 600°C to form a composite structure with a low-temperature transformation phase consisting of ferrite with a volume content of 40 to 75% and the remainder consisting of martensite, bainite, or a mixed structure of these. A method for producing a high-tensile steel wire bar that has excellent workability and does not require heat treatment, which is characterized by heating within a range.
度範囲から平均冷却速度１〜１５℃／秒にて２００℃未
満の温度範囲まで冷却して、体積含有率４０〜７５％の
フェライトと残部がマルテンサイト、ベイナイト又はこ
れらの混合組織からなる低温変態生成相との複合組織と
なし、次いで、２００〜６００℃の温度範囲に加熱する
ことを特徴とする加工性のすぐれた熱処理省略型高張力
線材棒鋼の製造方法。(5) A steel containing (a) C 0.05 to 0.20%, Si 1.0% or less, Mn 1.0 to 2.5%, and Ni 1.0% or less is heated by weight. After processing, it is cooled from a temperature range of 800 to 950 degrees Celsius to a temperature range of less than 200 degrees Celsius at an average cooling rate of 1 to 15 degrees Celsius/second to form ferrite with a volume content of 40 to 75% and the balance being martensite and bainite. Or, a method for producing a high-tensile steel wire bar with excellent workability without heat treatment, characterized by forming a composite structure with a low-temperature transformation formed phase consisting of a mixed structure of these, and then heating to a temperature range of 200 to 600°C. .
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP25298584A JPS61130424A (en) | 1984-11-29 | 1984-11-29 | Production of heat treatment-omission type high tension steel wire or rod having excellent workability |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP25298584A JPS61130424A (en) | 1984-11-29 | 1984-11-29 | Production of heat treatment-omission type high tension steel wire or rod having excellent workability |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPS61130424A true JPS61130424A (en) | 1986-06-18 |
Family
ID=17244898
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP25298584A Pending JPS61130424A (en) | 1984-11-29 | 1984-11-29 | Production of heat treatment-omission type high tension steel wire or rod having excellent workability |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS61130424A (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN114657334A (en) * | 2022-03-25 | 2022-06-24 | 西宁特殊钢股份有限公司 | Annealing process of mining circular chain steel 23MnNiMoCr54 with both structure control and hardness control |
Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5623223A (en) * | 1979-07-31 | 1981-03-05 | Nippon Steel Corp | Production of high-young's modulus steel material |
| JPS5831025A (en) * | 1981-08-14 | 1983-02-23 | Nippon Steel Corp | Production of high strength and high toughness steel |
-
1984
- 1984-11-29 JP JP25298584A patent/JPS61130424A/en active Pending
Patent Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5623223A (en) * | 1979-07-31 | 1981-03-05 | Nippon Steel Corp | Production of high-young's modulus steel material |
| JPS5831025A (en) * | 1981-08-14 | 1983-02-23 | Nippon Steel Corp | Production of high strength and high toughness steel |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN114657334A (en) * | 2022-03-25 | 2022-06-24 | 西宁特殊钢股份有限公司 | Annealing process of mining circular chain steel 23MnNiMoCr54 with both structure control and hardness control |
| CN114657334B (en) * | 2022-03-25 | 2023-11-17 | 西宁特殊钢股份有限公司 | Annealing process of mining round-link chain steel 23MnNiMoCr54 with structure control and hardness control |
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