JPS6158526B2 - - Google Patents
Info
- Publication number
- JPS6158526B2 JPS6158526B2 JP58026628A JP2662883A JPS6158526B2 JP S6158526 B2 JPS6158526 B2 JP S6158526B2 JP 58026628 A JP58026628 A JP 58026628A JP 2662883 A JP2662883 A JP 2662883A JP S6158526 B2 JPS6158526 B2 JP S6158526B2
- Authority
- JP
- Japan
- Prior art keywords
- temperature
- hot rolling
- slow cooling
- hot
- steel strip
- 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.)
- Expired
Links
- 238000005098 hot rolling Methods 0.000 claims description 10
- 229910001105 martensitic stainless steel Inorganic materials 0.000 claims description 6
- 229910001566 austenite Inorganic materials 0.000 claims description 4
- 238000000034 method Methods 0.000 claims description 4
- 230000009466 transformation Effects 0.000 claims description 4
- 238000010438 heat treatment Methods 0.000 claims description 3
- 229910000859 α-Fe Inorganic materials 0.000 claims description 2
- 238000000137 annealing Methods 0.000 description 11
- 238000010583 slow cooling Methods 0.000 description 11
- 229910000831 Steel Inorganic materials 0.000 description 7
- 239000010959 steel Substances 0.000 description 7
- 238000001816 cooling Methods 0.000 description 6
- 239000000463 material Substances 0.000 description 5
- 229910000734 martensite Inorganic materials 0.000 description 2
- 238000005096 rolling process Methods 0.000 description 2
- 238000005097 cold rolling Methods 0.000 description 1
- 238000007796 conventional method Methods 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- 238000002474 experimental method Methods 0.000 description 1
- 239000000203 mixture Substances 0.000 description 1
- 230000003647 oxidation Effects 0.000 description 1
- 238000007254 oxidation reaction Methods 0.000 description 1
- 230000000737 periodic effect Effects 0.000 description 1
- 238000001953 recrystallisation Methods 0.000 description 1
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
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
Description
本発明はマルテンサイトステンレス鋼の熱延鋼
帯の熱処理法に関するもので、冷間圧延などの可
能な軟化焼鈍を省略することを目的とするもので
ある。
従来、マルテンサイトステンレス鋼の熱延鋼帯
を得るには900℃を超え950℃未満の温度で熱間圧
延を終了し、コイル状に巻取後常温まで放冷する
が、約350℃付近でオーステナイト相がマルテン
サイト相に変態する。マルテンサイト相は硬さが
Hv>600と硬く、延性、靭性も低いため鋼帯の展
開が不可能である。このため一般的には、巻姿の
まゝ焼鈍(通常、ベル焼鈍と称す)を実施してい
る。
このベル焼鈍は常温より巻姿のまゝ850〜890℃
の高温で5〜15Hrと長時間保持後、変態完了温
度まで徐冷するが、通常鋼帯の場合は6〜12トン
の巻取状となつており、マスが大きいため中心部
まで目標温度とするには昇温のため長時間を要し
大量の熱エネルギーを必要とするばかりでなく、
高温加熱のため炉の内筒が消耗、変形し定期的に
取替が必要であるなどコストを要しさらには徐冷
速度を10〜30℃/Hrとするので、上記ベル焼鈍は
合計60〜100Hrに及ぶ長時間を必要としている。
以上のようにベル焼鈍はエネルギー的にも、工
程的にもロスが多く比較的低価格であるマルテン
サイトステンレス鋼の価格構成上、大きな比率を
占めているにも拘らず、ベル焼鈍は軟化を目的と
してオーステナイト相からのフエライト相+カー
バイド変態を完全にするため実施されるものであ
るため改善不可能の印象が強く何ら対策を採られ
ることなく現在に到つている。
本発明者らの実験によれば熱間圧延直後に再結
晶組織を有し、その後の徐冷において徐冷開始温
度が780℃以上であればベル焼鈍を省略し得るこ
とを知見した。
以下、この点に関し詳細に述べると、第1図に
示した硬さに及ぼす徐冷開始温度の関係の結果よ
り明らかなように徐冷開始温度は軟化の程度に大
きな影響を及ぼしており、徐冷開始温度が高いほ
ど何れの冷却速度においても軟化している。一方
マルテンサイトステンレス鋼の冷延可能な硬さは
Hv200以下程度であり、図面より明らかなように
冷却速度30℃/Hrの場合、780℃以上の徐冷開始
温度で、この値を満足させるが、780℃以下で徐
冷を開始した場合は冷却可能な硬さが得られな
い。
又、熱間加工温度と再結晶の関係を調査した結
果、熱間加工を950゜〜1280℃で実施することに
より再結晶組織が得られることを確認した。
従つて熱延終止温度を950℃以上に確保して再
結晶組織とし、その後のハンドリングを速やかに
行ない、徐冷炉に入れ前述のように780℃以上の
温度から徐冷すれば冷延可能な熱延鋼帯を得るこ
とができ、ベル焼鈍を完全に省略できる。
熱延終止温度は前述の通り950℃以上であれば
再結晶組織が得られるので950℃以上の温度で実
施するが、1280℃を超えると激しい酸化のために
スケールが発生して熱延不可能となるので、上限
は1280℃とする。しかし実際には1100℃以下とす
るのが望ましく、これはこれ以上の温度では再結
晶オーステナイト粒が粗大化する可能性が生ずる
ので熱延終止温度は950゜〜1280℃、好ましくは
950℃〜1100℃とする
以下、本発明の特徴を実施例に基いて説明す
る。
刃物用材などに使用される下記第1表に示す
SUS420J2鋼について、本発明法を適用した場合
の実施例について述べる。供試材はAOD炉で溶
解された連続鋳造スラブである。
The present invention relates to a heat treatment method for a hot-rolled martensitic stainless steel strip, and its purpose is to omit possible softening annealing such as cold rolling. Conventionally, to obtain a hot-rolled martensitic stainless steel strip, hot rolling is completed at a temperature of more than 900°C but less than 950°C, and after being coiled into a coil, it is allowed to cool to room temperature, but at around 350°C The austenite phase transforms into the martensite phase. The martensitic phase has hardness
It is hard (Hv > 600) and has low ductility and toughness, making it impossible to develop steel strips. For this reason, generally, annealing (usually referred to as bell annealing) is performed while the roll is in the form. This bell annealing is performed at 850 to 890 degrees Celsius while keeping the rolled form from room temperature.
After holding the steel strip at a high temperature for a long time (5 to 15 hours), it is slowly cooled to the transformation completion temperature.However, in the case of normal steel strip, it is rolled into a roll of 6 to 12 tons, and because the mass is large, it is necessary to reach the target temperature all the way to the center. Not only does it take a long time to raise the temperature and a large amount of thermal energy is required,
Due to the high temperature heating, the inner cylinder of the furnace wears out and deforms, requiring periodic replacement, which is costly.Furthermore, the annealing rate is set at 10 to 30℃/Hr, so the bell annealing described above requires a total of 60~ It requires a long time of up to 100 hours. As mentioned above, bell annealing involves a lot of energy and process loss, and although it occupies a large proportion of the price structure of relatively low-priced martensitic stainless steel, bell annealing does not cause softening. Since the purpose was to complete the transformation from austenite phase to ferrite phase + carbide, there was a strong impression that improvement was impossible, and no countermeasures have been taken to date. According to experiments conducted by the present inventors, it has been found that bell annealing can be omitted if the steel has a recrystallized structure immediately after hot rolling and the slow cooling start temperature is 780° C. or higher in subsequent slow cooling. This point will be discussed in detail below.As is clear from the relationship between the slow cooling start temperature and the hardness shown in Figure 1, the slow cooling start temperature has a large effect on the degree of softening, and The higher the cooling start temperature, the softer it becomes at any cooling rate. On the other hand, the hardness of martensitic stainless steel that can be cold rolled is
Hv200 or less, and as is clear from the drawing, if the cooling rate is 30℃/Hr, this value will be satisfied with a slow cooling start temperature of 780℃ or higher, but if slow cooling starts at 780℃ or lower, Possible hardness is not achieved. Furthermore, as a result of investigating the relationship between hot working temperature and recrystallization, it was confirmed that a recrystallized structure can be obtained by performing hot working at 950° to 1280°C. Therefore, the hot rolled material can be cold rolled by ensuring the final hot rolling temperature is 950°C or higher to obtain a recrystallized structure, followed by prompt handling, and then placing it in a slow cooling furnace and slowly cooling it from a temperature of 780°C or higher as described above. A steel strip can be obtained, and bell annealing can be completely omitted. As mentioned above, the end temperature of hot rolling is 950°C or higher because a recrystallized structure can be obtained, but if it exceeds 1280°C, scale will occur due to severe oxidation and hot rolling will not be possible. Therefore, the upper limit is set to 1280℃. However, in reality, it is desirable to set the temperature to 1,100°C or less, because if the temperature is higher than this, the recrystallized austenite grains may become coarse, so the hot rolling end temperature should be 950° to 1,280°C, preferably 1,280°C.
950° C. to 1100° C. Characteristics of the present invention will be explained below based on Examples. Table 1 below shows the materials used for cutlery materials, etc.
An example will be described in which the method of the present invention is applied to SUS420J2 steel. The specimen material is a continuously cast slab melted in an AOD furnace.
【表】
本例においては熱間圧延時、25〜30%の圧延比
率で終止温度を950℃以上の狙いで実績として970
℃で制御圧延し、巻取後速やかに徐冷炉に移す。
この間120〜140℃の温度低下はあるが、800〜820
℃から徐冷を開始し、変態完了温度の650℃まで
10〜30℃/Hrの冷却速度で徐冷後放冷した。
得られた鋼板の機械的性質を下記第2表に従来
材と比較して示す。[Table] In this example, during hot rolling, with a rolling ratio of 25 to 30%, the final temperature was aimed at 950℃ or higher, and the actual temperature was 970℃.
Controlled rolling is carried out at ℃ and immediately transferred to a slow cooling furnace after coiling.
During this time, there is a temperature drop of 120-140℃, but the temperature is 800-820℃.
Start slow cooling from ℃ to 650℃ which is the completion temperature of transformation.
After slow cooling at a cooling rate of 10 to 30°C/Hr, the mixture was left to cool. The mechanical properties of the obtained steel plate are shown in Table 2 below in comparison with conventional materials.
【表】
こゝにおいて従来法とは通常の熱延後室温まで
空冷後ベル焼鈍したものである。[Table] Here, the conventional method involves bell annealing after air cooling to room temperature after normal hot rolling.
第1図は硬さに及ぼす徐冷開始温度の影響を示
した図表である。
FIG. 1 is a chart showing the influence of slow cooling start temperature on hardness.
Claims (1)
止温度を950゜〜1280℃となるように制御熱延を
行ない、そのまゝ780℃以上の温度からオーステ
ナイト→フエライト+カーバイド変態完了温度ま
で徐冷することを特徴とするマルテンサイトステ
ンレス鋼の熱延鋼帯の熱処理法。1. Perform controlled hot rolling to obtain a martensitic stainless steel strip so that the final temperature of hot rolling is 950° to 1280°C, and then slowly cool from a temperature of 780°C or higher to the completion temperature of austenite → ferrite + carbide transformation. A heat treatment method for hot-rolled martensitic stainless steel strip characterized by:
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP2662883A JPS59153830A (en) | 1983-02-19 | 1983-02-19 | Heat treatment of hot rolled strip of martensitic stainless steel |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP2662883A JPS59153830A (en) | 1983-02-19 | 1983-02-19 | Heat treatment of hot rolled strip of martensitic stainless steel |
Publications (2)
Publication Number | Publication Date |
---|---|
JPS59153830A JPS59153830A (en) | 1984-09-01 |
JPS6158526B2 true JPS6158526B2 (en) | 1986-12-12 |
Family
ID=12198715
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
JP2662883A Granted JPS59153830A (en) | 1983-02-19 | 1983-02-19 | Heat treatment of hot rolled strip of martensitic stainless steel |
Country Status (1)
Country | Link |
---|---|
JP (1) | JPS59153830A (en) |
Families Citing this family (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP2745839B2 (en) * | 1991-03-01 | 1998-04-28 | 住友金属工業株式会社 | Manufacturing method of martensitic stainless steel slab |
FR2764669B1 (en) * | 1997-06-13 | 1999-07-16 | Coflexip | METHOD FOR MANUFACTURING A FLEXIBLE PIPE |
KR100523107B1 (en) * | 2000-06-23 | 2005-10-19 | 주식회사 포스코 | Method for heat treating hot rolled 420-type martensitic stainless steel |
Citations (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS5295527A (en) * | 1976-02-06 | 1977-08-11 | Sumitomo Metal Ind Ltd | Production of ferritic stainless steel sheet having good forming prope rty |
JPS5570404A (en) * | 1978-11-24 | 1980-05-27 | Nisshin Steel Co Ltd | Manufacture of hot coil of austenitic stainless steel |
JPS5770232A (en) * | 1980-10-20 | 1982-04-30 | Nippon Steel Corp | Production of ferritic stainless steel sheet having excellent workability |
-
1983
- 1983-02-19 JP JP2662883A patent/JPS59153830A/en active Granted
Patent Citations (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS5295527A (en) * | 1976-02-06 | 1977-08-11 | Sumitomo Metal Ind Ltd | Production of ferritic stainless steel sheet having good forming prope rty |
JPS5570404A (en) * | 1978-11-24 | 1980-05-27 | Nisshin Steel Co Ltd | Manufacture of hot coil of austenitic stainless steel |
JPS5770232A (en) * | 1980-10-20 | 1982-04-30 | Nippon Steel Corp | Production of ferritic stainless steel sheet having excellent workability |
Also Published As
Publication number | Publication date |
---|---|
JPS59153830A (en) | 1984-09-01 |
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