JPS59166626A - Continuous spheroidizing heat treatment of rod steel - Google Patents
Continuous spheroidizing heat treatment of rod steelInfo
- Publication number
- JPS59166626A JPS59166626A JP3750883A JP3750883A JPS59166626A JP S59166626 A JPS59166626 A JP S59166626A JP 3750883 A JP3750883 A JP 3750883A JP 3750883 A JP3750883 A JP 3750883A JP S59166626 A JPS59166626 A JP S59166626A
- Authority
- JP
- Japan
- Prior art keywords
- rod steel
- steel bar
- temperature
- furnace
- steel
- 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
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
-
- 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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/26—Methods of annealing
- C21D1/32—Soft annealing, e.g. spheroidising
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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 Articles (AREA)
- Heat Treatment Of Strip Materials And Filament Materials (AREA)
Abstract
Description
【発明の詳細な説明】
本発明は、所定の長さに切断した棒鋼を連続的に球状化
処理する方法、および製造に関するものである。DETAILED DESCRIPTION OF THE INVENTION The present invention relates to a method for continuously spheroidizing a steel bar cut to a predetermined length, and to manufacturing the same.
従来、冷間鍛造性が要求される棒鋼は、球状1ヒ処理が
施されているが、この処理には、例えば20時間という
ような長い処理時間を要していた。これに対し、特開昭
57−23026によシ新たに棒鋼線材の球状比処理方
法が提案されている。この方法を用いるならば、例えば
20分というような極めて短い処理時間で球状比が可能
となる。すなわち、第1図に示したように、素材’iA
c、+30℃〜AC+150℃の間の最高加熱温度(T
1)まで急速に加熱し、次いで、 Ar1変態点まで冷
却し、その後Ar1変態点以下の温度(T2)に保持す
るか、あるいは徐冷すれば、素材を十分軟[ヒさせるこ
とが可能である。Conventionally, steel bars that require cold forgeability have been subjected to spherical 1H treatment, but this treatment required a long treatment time, for example, 20 hours. In response to this, a new method for treating the spherical ratio of steel wire rods has been proposed in JP-A-57-23026. Using this method, a spherical ratio can be achieved in a very short processing time, for example 20 minutes. That is, as shown in FIG.
c, maximum heating temperature between +30℃ and AC+150℃ (T
It is possible to soften the material sufficiently by rapidly heating it to 1), then cooling it to the Ar1 transformation point, and then maintaining it at a temperature (T2) below the Ar1 transformation point, or slowly cooling it. .
本発明は、上記先行発明におけるこの原理を棒鋼材、特
に機械構造用炭素鋼、合金鋼の軟化処理に適用する場合
の具体的な方法に係わるものである。この場合、特に問
題になる点は、棒鋼の軸方向における中心部と、表面並
びに長手方向における中央部と先端部とで温度むらが生
ずることである。The present invention relates to a specific method for applying this principle in the above-mentioned prior invention to the softening treatment of steel bars, particularly carbon steel for mechanical structures and alloy steel. In this case, a particular problem is that temperature unevenness occurs between the center in the axial direction, the surface, and the center and tip in the longitudinal direction.
また、棒鋼に対する最適な最高加熱温度(T1)は、鋼
種、加熱速度によって決まるが、特に機械構造用炭素鋼
、合金鋼において十分な冷鍛性を得るためにはs Tt
のばらつきを30℃以内におさえる必要がある。第2図
には、5Or440の棒鋼(10mmφ)を図示の条件
で熱処理した彼、片
8φX12H(mm)の試験席を作製して冷間で鍛造試
験を行なったときの最高加熱温度(T1)と冷間鍛造割
れ発生限界圧縮率(%)の関係を示すグラフであるが%
”Iが790℃〜820℃の場合に特に良い冷鍛性を
示している。また第3図は8400の鋼材について第2
図のものと同一試験を行なった場合の同様な関係を示す
グラフであって、この場合にはT1が750℃〜780
℃であるときに特に良い冷鍛性を示している。In addition, the optimal maximum heating temperature (T1) for steel bars is determined by the steel type and heating rate, but in order to obtain sufficient cold forgeability, especially for carbon steels and alloy steels for machine structures, s Tt
It is necessary to suppress the variation in temperature to within 30°C. Figure 2 shows the maximum heating temperature (T1) when a 5Or440 steel bar (10mmφ) was heat-treated under the conditions shown, and a cold forging test was conducted using a test bench of 8φ×12H (mm). This is a graph showing the relationship between cold forging crack occurrence limit compression ratio (%).
"I shows particularly good cold forging properties when I is between 790°C and 820°C. Also, Figure 3 shows that the cold forging properties of 8400 steel
This is a graph showing a similar relationship when the same test as that shown in the figure was conducted, and in this case, T1 was 750°C to 780°C.
It shows particularly good cold forging properties when the temperature is ℃.
以上の事実によれば、両鋼種いづれの場合でもT、の許
容偏差範囲は30℃であることが分かる。According to the above facts, it can be seen that the allowable deviation range of T is 30°C for both steel types.
したがって、棒鋼を急速球状rヒ処理するには、棒鋼内
におけるT、のばらつきの幅を30℃以内におさめるこ
とが必要となる。Therefore, in order to subject a steel bar to rapid spherical heat treatment, it is necessary to keep the variation in T within the steel bar within 30°C.
しかして、第4図は、棒鋼(36rnmφ)全ガスバー
ナで加熱した際の棒鋼表面と中心部における昇温特性を
示すグラフである。これによれば、両者間で非常に大き
な温度差が生じておシ、この場合には、表面と中心部の
最高加熱温度(T□)の差を30℃以内に抑えることは
不可能であることが分かる。Therefore, FIG. 4 is a graph showing the temperature rise characteristics at the surface and center of a steel bar (36 nmφ) when heated with a full gas burner. According to this, a very large temperature difference occurs between the two, and in this case, it is impossible to suppress the difference in the maximum heating temperature (T□) between the surface and the center to within 30°C. I understand that.
これに対し、第5図は、第4図の場合のものと同一素材
からなる棒鋼を誘導加熱炉により急速加熱した場合の同
様な箇所における昇温特性を示すグラフであって、この
場合には、表面と中心部との温度差は非常に小さく、シ
たがって、両者間の最高加熱温度(T8)の差を30℃
以内に抑えることが可能なことが分かる。On the other hand, FIG. 5 is a graph showing the temperature rise characteristics at a similar location when a steel bar made of the same material as in FIG. 4 is rapidly heated in an induction heating furnace. , the temperature difference between the surface and the center is very small, so the difference in maximum heating temperature (T8) between the two is 30°C.
It can be seen that it is possible to keep it within the range.
このように、棒鋼中心部と表面の温度差は、誘導加熱全
採用することによシ、十分小さくすることができる。し
かしながら従来、誘導加熱を用いる場合に棒鋼の両端部
の温度が中央部の温度よシ低くなることが知られている
。この点の問題は、誘導加熱の周波数を高くすることに
よって解決できるが、周波数を高くすると、いわゆる表
皮効果が大きくなって棒鋼の表面と中心部間の温度差が
大きくなってしまう。In this way, the temperature difference between the center and the surface of the steel bar can be made sufficiently small by fully employing induction heating. However, it is conventionally known that when induction heating is used, the temperature at both ends of the steel bar is lower than the temperature at the center. This problem can be solved by increasing the frequency of induction heating, but increasing the frequency increases the so-called skin effect and increases the temperature difference between the surface and center of the steel bar.
また第5図について述べたように、誘導加熱を採用して
表面と中心部間の温度差を十分小さくする場合には、な
お棒鋼の直径に応じた最適の周波数が存在する。Further, as described with reference to FIG. 5, when induction heating is used to sufficiently reduce the temperature difference between the surface and the center, there is still an optimum frequency depending on the diameter of the steel bar.
しかし、本発明者によシ笑験を行なったところ、その周
波数では棒鋼の両端部の温度が中央部のそれよりも低く
なり、長手方向にわたって温度むらが生じていることが
知見された。However, when the present inventor conducted experiments, it was found that at that frequency, the temperature at both ends of the steel bar was lower than that at the center, and temperature unevenness occurred in the longitudinal direction.
そこで、この温度むらの問題全解決すべく更に実験を重
ねたところ、つぎに述べるような事実が知見された。Therefore, we conducted further experiments in order to completely solve the problem of temperature unevenness, and the following fact was discovered.
まず、棒鋼全誘導加熱炉内に間欠的に一定の送9長さで
送シ込むことによって、加熱炉内での41鋼の両端部の
位置金常に一定としたうえ、誘導コイルの巻数を調製す
る等の操作全行なって両端部に付加する熱tit’を多
くしたところ、棒鋼全長にわたシ比較的均一な温度に加
熱できることが分かった。First, by intermittently feeding the steel bar into the induction heating furnace at a constant feed length, the position of both ends of the steel bar in the heating furnace was always constant, and the number of turns of the induction coil was adjusted. By performing all of the above operations to increase the heat tit' applied to both ends, it was found that the steel bar could be heated to a relatively uniform temperature over its entire length.
しかし、上記の方法だけでは棒鋼長手方向にわたる各位
置の最高加熱温度T1のばらつき幅を30℃以内に抑え
ることはできなかった。すなわち、第6図は、36φX
200Lの棒鋼を誘導加熱炉で間欠送シして加熱した際
の両端部(1)。However, using only the above method, it was not possible to suppress the variation width of the maximum heating temperature T1 at each position in the longitudinal direction of the steel bar to within 30°C. That is, Fig. 6 shows 36φX
Both ends (1) of a 200L steel bar heated by intermittent feeding in an induction heating furnace.
(3)と中央部(2)の昇温特注ヲ示したグラフであっ
て、間欠送り方式の採用により、加熱時間がはソ80秒
、加熱温度が750’Cを超えてゆくと、(1) 、
(2) 、 (a)の各位置の温度はほとんど一致して
いるが、加熱時間が140秒を超えると先端部(1)の
温度だけが低下してゆき、中央部(2)、後端部(3)
は昇温全続け、これにより(1)〜(3)間の最高加熱
温度の差は70℃にも達している。この現象は、棒鋼全
誘導コイル内から徐々に取り出しているために、棒鋼先
端部のみが誘導コイルから外へ出て加熱が停止する一方
、他の部分はなお加熱されるためである。この加熱不均
一を解消すべく、誘導コイルの巻き数や、コイル内での
棒鋼の位置を種々変えてみたが、棒鋼全加熱炉から徐々
に取り出している限)、上記の問題を解決できないこと
が分かった。そこで、棒鋼を間欠的に誘導加熱炉内に送
シ込むとともに、棒鋼を加熱炉から一気に取シ出す実験
を行なった。This is a graph showing a custom-made temperature increase for (3) and the center part (2). By adopting the intermittent feed method, the heating time is 80 seconds, and when the heating temperature exceeds 750'C, (1 ),
The temperatures at each position (2) and (a) are almost the same, but when the heating time exceeds 140 seconds, only the temperature at the tip (1) decreases, and the temperature at the center (2) and rear end decreases. Part (3)
The temperature continued to rise, and as a result, the difference in maximum heating temperature between (1) to (3) reached 70°C. This phenomenon occurs because the entire steel bar is gradually taken out from within the induction coil, so only the tip of the steel bar comes out of the induction coil and heating stops, while other parts are still heated. In order to eliminate this uneven heating, we tried variously changing the number of turns of the induction coil and the position of the steel bar within the coil, but as long as all the bars were gradually removed from the heating furnace, the above problem could not be solved. I understand. Therefore, an experiment was conducted in which the steel bars were intermittently fed into the induction heating furnace and the steel bars were removed from the heating furnace all at once.
すなわち、第7図は、この場合の実験として第6図の場
合と同一の鋼材を誘導加熱炉に間欠的に送り込んで加熱
し、ついで加熱炉からこれを一気に取シ出した場合((
おける第6図と同様な棒鋼各位置の昇温特注を示したグ
ラフである。In other words, Fig. 7 shows an experiment in which the same steel material as in Fig. 6 was intermittently fed into an induction heating furnace and heated, and then removed from the heating furnace all at once ((
6 is a graph showing a custom temperature increase at each position of the steel bar, similar to FIG. 6 in FIG.
これから明らかなように、棒鋼の長手方向の最高加熱温
度T、のばらつきは非常に小さい。したがって、誘導加
熱において間欠送シと一気取シ出しの方式を採用するな
らば、棒鋼の長手方向にわたシ中心部と表面部間ならび
に両端部間においてT1の差を30℃以内に抑えられる
ことがわかった。As is clear from this, the variation in the maximum heating temperature T in the longitudinal direction of the steel bars is very small. Therefore, if the intermittent feeding and all-at-once methods are adopted for induction heating, the difference in T1 between the center and the surface of the steel bar in the longitudinal direction, as well as between both ends, can be suppressed to within 30°C. I understand.
本発明は、このような知見から発明されたものであり、
本発明により始めて棒鋼全体を均一に加熱することが可
能となる。The present invention was invented based on such knowledge,
The present invention makes it possible for the first time to uniformly heat the entire steel bar.
本発明は、所定の長さに切断した棒鋼を誘導加熱炉内に
間欠的に一定の送シ長さで送り込み、棒鋼をAc1 +
30℃〜AcI +80℃の最高加熱温度に急速加熱
した後、誘導加熱炉から一気に取出し、これによって棒
鋼内における最高加熱温度の差金30℃以内に抑え、次
いで、650℃〜710℃の温度に保持した炉内に順次
送り込むこと全特徴とするものである。In the present invention, a steel bar cut to a predetermined length is intermittently fed into an induction heating furnace at a constant feeding length, and the steel bar is heated to Ac1 +
After rapidly heating to a maximum heating temperature of 30°C to AcI +80°C, the steel bar is taken out at once from the induction heating furnace, thereby keeping the difference in maximum heating temperature within the steel bar within 30°C, and then maintained at a temperature of 650°C to 710°C. The main feature is that the materials are sequentially fed into the furnace.
第8図は、ヒートパターンを第7図のようにして本発明
の方法によシ、球状比処理した20φx20OLの棒鋼
(SOr40)の冷鍛性を比較方法として、ヒートパタ
ーンを第6図のようにして間欠送りで加熱を行なうが、
炉からの取出しは一気に行わないで球状1ヒ処理を行な
った同一鋼材の冷鍛性と比較して示すグラフである。こ
れによれば、本発明の方法によシ処理された棒限界圧縮
率(75チを超える)を示している。Figure 8 is a comparison method of the cold forgeability of a 20φ x 20OL steel bar (SOr40) that has been subjected to spherical ratio treatment according to the method of the present invention with the heat pattern as shown in Figure 7, and the heat pattern as shown in Figure 6. Heating is performed with intermittent feed, but
This is a graph showing a comparison of the cold forgeability of the same steel material which was subjected to spherical treatment without being taken out from the furnace all at once. This shows the critical compression ratio (exceeding 75 inches) of rods processed by the method of the present invention.
縮率は62.5%であって明らかに不良である。The shrinkage rate was 62.5%, which is clearly poor.
したがって、本発明のように誘導加熱、間欠送り、−気
取出しの3条件を組合わせることによって、始めて棒鋼
全長にわたって良好な冷鍛性が得られることが明らかで
ある。Therefore, it is clear that good cold forgeability can be obtained over the entire length of the steel bar by combining the three conditions of induction heating, intermittent feeding, and air extraction as in the present invention.
最高加熱温度T1は前組織のパーライトがオーステナイ
ト化し、球状化炭[ヒ物の核が残った組織となる温度で
あ、り、Ac、+301:、 〜Ac、+8(1℃であ
る。さらに詳しく述べると、この範囲は鋼種によって異
なシ、機械構造用炭素鋼の棒材ではAc、+30℃〜A
c1+60℃であり、機械構造用合金鋼の棒材ではAc
、+40℃〜AC1+80℃である。The maximum heating temperature T1 is the temperature at which the pearlite in the previous structure becomes austenite and becomes a structure in which the core of spheroidized carbon remains. In other words, this range differs depending on the steel type, and for carbon steel bars for machine structures, it is Ac, +30℃~A
c1 + 60℃, and for machine structural alloy steel bars, Ac
, +40°C to AC1 +80°C.
これらの温度よりもT+e低くすると前組織のツク−ラ
イトが処理後まで残り、冷鍛性が改善されないし、高く
すると再生パーライトが析出し、冷鍛性が劣[ヒする。If T+e is lower than these temperatures, the tsukurite of the previous structure will remain until after the treatment, and cold forgeability will not be improved; if it is higher than these temperatures, recycled pearlite will precipitate, resulting in poor cold forgeability.
保持炉においてはAr、変態点直下に保持もしくは徐冷
するが、保持炉温’t650〜710℃とする事によっ
て達成できる。In the holding furnace, Ar is used to maintain or slowly cool the temperature just below the transformation point, which can be achieved by setting the holding furnace temperature to 650 to 710°C.
以下、本発明を実施する装置の一例をのべる。An example of an apparatus for implementing the present invention will be described below.
第9図は、本発明を実施する鋼材処理装置の配置図を示
す。供給シュート2に載せた棒鋼1は、押込ピストン3
によって間欠的に高周波誘導加熱炉4内に送シ込まれる
。所定の最高温度に加熱された後、棒鋼は、加熱炉4出
口で一気取出し機構5(チェーンと押さえロールから成
っている。)によって−気に取シ出され、ついで押し出
しピストン6によって恒温保持炉7に送り込まれる。保
持炉7内には2本のレールが勾配を以って平行に敷かれ
ておシ、送シ込まれた棒鋼はこのレール上を転がって炉
の出口方向に進む。また保持炉7出口には、棒鋼の取シ
出し機構が設けられておシ、一定の時間間隔で棒鋼が1
本づつ取シ出される。FIG. 9 shows a layout diagram of a steel processing apparatus that implements the present invention. The steel bar 1 placed on the supply chute 2 is pushed into the pushing piston 3
It is intermittently fed into the high frequency induction heating furnace 4 by. After being heated to a predetermined maximum temperature, the steel bar is taken out at once at the outlet of the heating furnace 4 by a take-out mechanism 5 (consisting of a chain and a pressure roll), and then transferred to a constant temperature holding furnace by an extrusion piston 6. Sent to 7. Inside the holding furnace 7, two rails are laid in parallel with a slope, and the fed steel bar rolls on these rails and advances toward the exit of the furnace. In addition, a steel bar take-out mechanism is installed at the outlet of the holding furnace 7, and one steel bar is removed at regular intervals.
Books are taken out one by one.
第1表は、上記の装置を用いて8400と5Or40の
それぞれ36φx 20 OLの棒鋼を、本発明の方法
と従来の方法とにょ勺それぞれ球状化処理した場合の処
理後の各棒鋼の機械的性質と球状化所要時間とを比較し
て示したものである。Table 1 shows the mechanical properties of the 8400 and 5Or40 steel bars of 36φ x 20OL after spheroidization using the method of the present invention and the conventional method using the above-mentioned apparatus. This figure shows a comparison of the time required for spheroidization and the time required for spheroidization.
第1表から、本発明によれば、棒鋼において従来方法に
よって処理されたもののそれに匹敵する機械的性質が2
0分という極めて短い処理時間で得られることが明らか
である。From Table 1, it can be seen that according to the present invention, the mechanical properties of the steel bar treated by the conventional method are comparable to those of the steel bar treated by the conventional method.
It is clear that this can be obtained in an extremely short processing time of 0 minutes.
第1図は急速球状rヒ処理におけるヒートノでターンを
模式的に示す図。
第2図は、急速球状[ヒ処理全施した5Or440の棒
鋼について最高加熱温度と冷間鍛造試験における割れ発
生限界圧縮率との関係全示す図表、第3図は同じ<84
00の棒鋼について同関係を示す図表、
第4図(は36φの棒鋼全ガスバーナーにより加熱した
際の棒鋼表面と中心の昇温特注を示す図表、
第5図は同棒鋼全誘導加熱によシ加熱した際の上記昇温
特性を示す図表、
第6図は36φx200Lの棒鋼を誘導加熱炉に間欠的
に送り込んで加熱した際の、長手力向各位置の昇温特性
を示す図表、
第7図は同棒鋼を間欠送シと一気取シ出しを採用して誘
導加熱炉によシ加熱した際の長手力向各位置の昇温特性
を示す図表、
第8図は、5Or440の20φX20OL棒鋼を本発
明方法及び比較方法によってそれぞれ処理した場合の、
長手力向各位置における割れ発生限界圧縮率を示す図表
、
第9図は、本発明の実施例に用いた球状比処理装置の概
略配置図である。
1・・・棒鋼、2・・・棒鋼供給シュート、3・・・押
し込みピストン、4・・・高周波誘導加熱炉、5・・・
−気取り出し機構、6・・・押し出しピストン、7・・
・恒温保持炉、8・・・インバータ、9・・・負荷整合
盤、10・・・操作盤。
代理人 鈴木惟司
第1図
時間(min’。
2図
最高力n熱温度T1(”C)
う図
最aもカロ熱)顛丁1(’C)
見4図
力口 奔恢 時 fL”](,5ec)苑5図
力口 熱 時 間 (sea>
賄間C5ec)
第δ艮
LjV利4宋η)(イ丁り置FIG. 1 is a diagram schematically showing a turn in a heat nozzle in a rapid spherical rhi process. Figure 2 is a chart showing the relationship between the maximum heating temperature and the critical compressibility for cracking in a cold forging test for a 5Or440 steel bar that has been fully subjected to rapid spherical treatment.
A chart showing the same relationship for a 00 steel bar, Figure 4 is a chart showing the custom temperature rise of the surface and center of the bar when heated by a full gas burner for a 36φ bar, and Figure 5 is a chart showing the custom temperature rise of the bar surface and center when heated by a full gas burner for the same bar. A chart showing the temperature rise characteristics mentioned above when heated. Fig. 6 is a chart showing the temperature rise characteristics at each position in the longitudinal direction when a 36φ x 200L steel bar is intermittently fed into an induction heating furnace and heated. Fig. 7 Figure 8 is a chart showing the temperature rise characteristics at each position in the longitudinal force direction when the same steel bar is heated in an induction heating furnace using intermittent feeding and sudden withdrawal. When processed by the invention method and comparative method, respectively,
FIG. 9 is a diagram showing the critical compressibility for cracking at each position in the longitudinal force direction. FIG. 9 is a schematic layout diagram of the spherical ratio processing device used in the embodiment of the present invention. DESCRIPTION OF SYMBOLS 1... Steel bar, 2... Steel bar supply chute, 3... Pushing piston, 4... High frequency induction heating furnace, 5...
- Air extraction mechanism, 6... Pushing piston, 7...
- Constant temperature holding furnace, 8... Inverter, 9... Load matching panel, 10... Operation panel. Agent Koji Suzuki Figure 1 Time (min'. Figure 2 Maximum force n Heat temperature T1 ("C) Figure 2 Maximum force n Heat temperature T1 ('C) Figure 4 Maximum power n Heat temperature T1 ('C) Figure 4 Power mouth Time fL"] (, 5ec) Garden 5 power mouth heat time (sea> bribe interval C5ec) 5th 艮LjV li 4 Songη) (I Ding place
Claims (1)
定の送9長さで送り込み、棒鋼をAc、 +30℃〜A
c、 + 80℃の最高加熱温度に急速加熱した後、前
記炉から一気に取出し、これによって棒鋼内における最
高加熱温度の差全30℃以内に抑え、次いで650℃〜
710℃の温度に保持した炉内に、順次送シ込むことを
特徴とする棒鋼の連続球状[ヒ熱処理方法。A steel bar cut to a predetermined length is intermittently fed into an induction heating furnace at a constant feeding length, and the steel bar is heated to AC, +30℃~A.
c. After rapidly heating to a maximum heating temperature of +80°C, take it out from the furnace at once, thereby suppressing the difference in maximum heating temperature within the steel bar to within 30°C, and then heating from 650°C to
A continuous spherical steel bar [heat treatment method] characterized by sequentially feeding the steel bar into a furnace maintained at a temperature of 710°C.
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP3750883A JPS59166626A (en) | 1983-03-09 | 1983-03-09 | Continuous spheroidizing heat treatment of rod steel |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP3750883A JPS59166626A (en) | 1983-03-09 | 1983-03-09 | Continuous spheroidizing heat treatment of rod steel |
Publications (2)
Publication Number | Publication Date |
---|---|
JPS59166626A true JPS59166626A (en) | 1984-09-20 |
JPH0447005B2 JPH0447005B2 (en) | 1992-07-31 |
Family
ID=12499468
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
JP3750883A Granted JPS59166626A (en) | 1983-03-09 | 1983-03-09 | Continuous spheroidizing heat treatment of rod steel |
Country Status (1)
Country | Link |
---|---|
JP (1) | JPS59166626A (en) |
Cited By (5)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US4865836A (en) * | 1986-01-14 | 1989-09-12 | Fluoromed Pharmaceutical, Inc. | Brominated perfluorocarbon emulsions for internal animal use for contrast enhancement and oxygen transport |
US5080885A (en) * | 1986-01-14 | 1992-01-14 | Alliance Pharmaceutical Corp. | Brominated perfluorocarbon emulsions for internal animal use for contrast enhancement and oxygen transport |
US5114703A (en) * | 1989-05-30 | 1992-05-19 | Alliance Pharmaceutical Corp. | Percutaneous lymphography using particulate fluorocarbon emulsions |
JPH05112809A (en) * | 1991-07-26 | 1993-05-07 | Mitsubishi Nagasaki Kiko Kk | Production of ultrahigh strength steel |
CN1089116C (en) * | 1999-04-30 | 2002-08-14 | 吴凡 | Carbide annealing process for high-speed great-deformation hot-rolled and cold-upset steel |
-
1983
- 1983-03-09 JP JP3750883A patent/JPS59166626A/en active Granted
Cited By (6)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US4865836A (en) * | 1986-01-14 | 1989-09-12 | Fluoromed Pharmaceutical, Inc. | Brominated perfluorocarbon emulsions for internal animal use for contrast enhancement and oxygen transport |
US5080885A (en) * | 1986-01-14 | 1992-01-14 | Alliance Pharmaceutical Corp. | Brominated perfluorocarbon emulsions for internal animal use for contrast enhancement and oxygen transport |
US5114703A (en) * | 1989-05-30 | 1992-05-19 | Alliance Pharmaceutical Corp. | Percutaneous lymphography using particulate fluorocarbon emulsions |
US5496536A (en) * | 1989-05-30 | 1996-03-05 | Wolf; Gerald | Percutaneous lymphography |
JPH05112809A (en) * | 1991-07-26 | 1993-05-07 | Mitsubishi Nagasaki Kiko Kk | Production of ultrahigh strength steel |
CN1089116C (en) * | 1999-04-30 | 2002-08-14 | 吴凡 | Carbide annealing process for high-speed great-deformation hot-rolled and cold-upset steel |
Also Published As
Publication number | Publication date |
---|---|
JPH0447005B2 (en) | 1992-07-31 |
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