JPS6386817A - Production of stainless clad steel - Google Patents
Production of stainless clad steelInfo
- Publication number
- JPS6386817A JPS6386817A JP23293486A JP23293486A JPS6386817A JP S6386817 A JPS6386817 A JP S6386817A JP 23293486 A JP23293486 A JP 23293486A JP 23293486 A JP23293486 A JP 23293486A JP S6386817 A JPS6386817 A JP S6386817A
- Authority
- JP
- Japan
- Prior art keywords
- steel
- thickness
- hot
- stainless
- cold rolling
- 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
- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 36
- 239000010959 steel Substances 0.000 title claims abstract description 36
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 16
- 238000005097 cold rolling Methods 0.000 claims abstract description 28
- 239000011162 core material Substances 0.000 claims abstract description 28
- 238000010438 heat treatment Methods 0.000 claims abstract description 24
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims abstract description 22
- 229910052799 carbon Inorganic materials 0.000 claims abstract description 22
- 239000000463 material Substances 0.000 claims abstract description 16
- 239000010935 stainless steel Substances 0.000 claims abstract description 16
- 229910001220 stainless steel Inorganic materials 0.000 claims abstract description 16
- 238000005304 joining Methods 0.000 claims abstract description 5
- 238000004804 winding Methods 0.000 claims abstract description 5
- 229910001315 Tool steel Inorganic materials 0.000 claims abstract description 3
- 238000000034 method Methods 0.000 claims description 12
- 238000005098 hot rolling Methods 0.000 claims description 7
- 230000013011 mating Effects 0.000 claims description 3
- 238000009792 diffusion process Methods 0.000 abstract description 15
- 229910000677 High-carbon steel Inorganic materials 0.000 abstract description 12
- 239000011248 coating agent Substances 0.000 abstract 1
- 238000000576 coating method Methods 0.000 abstract 1
- 238000005336 cracking Methods 0.000 abstract 1
- 238000005261 decarburization Methods 0.000 description 7
- 238000007747 plating Methods 0.000 description 5
- 238000005253 cladding Methods 0.000 description 4
- 239000002184 metal Substances 0.000 description 4
- 229910052751 metal Inorganic materials 0.000 description 4
- 238000005516 engineering process Methods 0.000 description 3
- 230000009466 transformation Effects 0.000 description 3
- 239000010960 cold rolled steel Substances 0.000 description 2
- 230000007423 decrease Effects 0.000 description 2
- 238000010586 diagram Methods 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- JEIPFZHSYJVQDO-UHFFFAOYSA-N iron(III) oxide Inorganic materials O=[Fe]O[Fe]=O JEIPFZHSYJVQDO-UHFFFAOYSA-N 0.000 description 2
- 238000005554 pickling Methods 0.000 description 2
- 239000000853 adhesive Substances 0.000 description 1
- 230000001070 adhesive effect Effects 0.000 description 1
- 238000000137 annealing Methods 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- 239000003610 charcoal Substances 0.000 description 1
- 238000007796 conventional method Methods 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 230000006866 deterioration Effects 0.000 description 1
- 238000009713 electroplating Methods 0.000 description 1
- 239000011888 foil Substances 0.000 description 1
- 239000002648 laminated material Substances 0.000 description 1
- 238000010030 laminating Methods 0.000 description 1
- 230000002265 prevention Effects 0.000 description 1
- 238000010791 quenching Methods 0.000 description 1
- 230000000171 quenching effect Effects 0.000 description 1
- 230000000630 rising effect Effects 0.000 description 1
- 238000005480 shot peening Methods 0.000 description 1
- 238000010583 slow cooling Methods 0.000 description 1
- 238000005496 tempering 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
Abstract
Description
【発明の詳細な説明】
〔産業上の利用分野〕
本発明はステンレスクラッド鋼の製造方法に係り、特に
接合面の炭素拡散移動を抑制し冷延時の芯材の亀裂を防
止できる製造方法に関する。DETAILED DESCRIPTION OF THE INVENTION [Industrial Application Field] The present invention relates to a method for manufacturing stainless clad steel, and more particularly to a method for manufacturing stainless clad steel that suppresses carbon diffusion and movement at joint surfaces and prevents cracks in the core material during cold rolling.
高炭素鋼と炭素含有量が低いステンレスε4をクラツド
鋼とすると、熱処理過程において高炭素鋼からステンレ
ス鋼へ炭素が拡散移動する問題があった。刃物用ステン
レスクラッド鋼て炭素の拡散移動が生ずると、切れ味の
劣化、ステンレス鋼の耐食性の低減および接合境界面が
不鮮明となることによる商品価値の低下等の問題がある
。When high carbon steel and stainless steel ε4 having a low carbon content are used as clad steel, there is a problem that carbon diffuses and moves from the high carbon steel to the stainless steel during the heat treatment process. When carbon diffusion and movement occurs in stainless steel clad steel for cutlery, there are problems such as deterioration of sharpness, reduction in corrosion resistance of stainless steel, and decrease in commercial value due to unclear joint interface.
この炭素の拡散移動を防止する技術が例えば金属表面技
術総覧(昭和47年2月20日、日刊工業新聞社発行、
第1097頁)に示さnている。Technologies for preventing this diffusion and movement of carbon include, for example, Metal Surface Technology Overview (February 20, 1971, published by Nikkan Kogyo Shimbun),
(page 1097).
これは高炭素鋼とステンレス鋼との接合前に(イ)高炭
素鋼またはステンレス11の接触面にNiまt:はFe
を電カフめっきする。(ロ)高炭素鋼とステンレス鋼と
の間にCr 5〜40%、Ni16〜5%その他から
なる金属層を挿入した状態で接合するというのである。This is done before joining high carbon steel and stainless steel.
Electroplating the cuff. (b) A metal layer consisting of 5 to 40% Cr, 16 to 5% Ni, etc. is inserted between high carbon steel and stainless steel before they are joined.
接合面にめっきあるいは金属層を挿入するこれらの方法
はある程度の効果は認められるが、大型鋼塊または大型
スラブを使用する場合に良好な結果を得ようとすればめ
っきあるいは金属層の厚さを相当厚くする必要があり、
これは価格が上り問題であった。また、大型鋼塊または
大型スラブに厚く一様にめっきするのは困難であり、厚
いめっきの場合は母材との接着力に問題があり冷延にお
いて剥離する懸念があった。These methods of inserting plating or metal layers on the joint surfaces are effective to some extent, but if you want to get good results when using large steel ingots or large slabs, it is necessary to increase the thickness of the plating or metal layer. It needs to be quite thick,
This caused the problem of rising prices. In addition, it is difficult to plate large steel ingots or large slabs thickly and uniformly, and in the case of thick plating, there is a problem with the adhesive strength with the base material, and there is a concern that it may peel off during cold rolling.
また、芯材が高炭素鋼、合せ材がステンレス鋼のクラッ
ド錆は鋳込法あるいは組立スラブから製造されるが、芯
材である高炭素鋼が冷延時に亀裂を発生するのも大きな
問題であった。In addition, cladding rust in which the core material is high carbon steel and the mating material is stainless steel is manufactured by casting or assembled slabs, but it is also a big problem that the high carbon steel core material cracks during cold rolling. there were.
本発明の目的は、上記従来技術の問題点を解決し、高炭
素1i1からステンレス鋼への炭素の拡散移動を防止し
、冷延における高炭素鋼の亀裂を防止できるステンレス
クラッドSηの製造方法を提供するにある。The purpose of the present invention is to provide a method for manufacturing stainless steel clad Sη that can solve the problems of the prior art described above, prevent carbon diffusion from high carbon 1i1 to stainless steel, and prevent cracks in high carbon steel during cold rolling. It is on offer.
〔問題点を解決するための手段および作用〕本発明の要
旨とするところは次の如くである。[Means and operations for solving the problems] The gist of the present invention is as follows.
すなわち、芯材を炭素工具錆鈎材5KI−5K5、合せ
材をステンレス鋼とする3層のステンレスクラッド鋼の
製造方法において、接合面に接合後の材料厚さの02〜
1%の厚さのNl膜を設ける工程と、コイル巻取温度を
600〜500℃の温度範囲とする熱間圧延工程と、冷
間圧延前に加熱温度および保持時間をそれぞれ座標軸と
する図面の下記座標A、B、C,D、E、F、G、Hで
囲まれる範囲内の加熱温度と保持時間で熱延鋼帯を熱処
理する工程と、を有して成ることを特徴とするステンレ
スクラッド鋼の製造方法である。That is, in a method for manufacturing three-layer stainless clad steel in which the core material is carbon tool rust hook material 5KI-5K5 and the mating material is stainless steel, the material thickness after joining on the joint surface is 02~
The drawing shows the process of providing a 1% thick Nl film, the hot rolling process in which the coil winding temperature is in the range of 600 to 500°C, and the heating temperature and holding time before cold rolling as the coordinate axes. A stainless steel product comprising the step of heat-treating a hot-rolled steel strip at a heating temperature and holding time within a range surrounded by the following coordinates A, B, C, D, E, F, G, and H. This is a method for manufacturing clad steel.
記
座標 加熱温度(℃) 保持時間(分)A
700
3B 750
2C7501
D 800
1E 850
1F 8
00 2G
800 3H
7503
接合面における炭素拡散移動を防止するためNi膜を設
けろことが効果的であるのは上記のとおりであるが、本
発明においては製造条件を限定することによりNi膜厚
を極力減少し、コストの低減を図った。すなわち、接合
面に設備う時の材料厚さの02〜1%の厚さのNi膜を
設ける。例えば100mm厚のスラブからクラツド鋼板
を製造する場合は200〜1000μmの厚さのめっき
を行うかもしくはNi箔を装入する。Coordinates Heating temperature (℃) Holding time (minutes) A
700
3B 750
2C7501 D 800
1E 850
1F 8
00 2G
800 3H
7503 As mentioned above, it is effective to provide a Ni film to prevent carbon diffusion and movement at the joint surface, but in the present invention, the Ni film thickness is reduced as much as possible by limiting the manufacturing conditions, and the cost is reduced. We aimed to reduce the That is, a Ni film having a thickness of 02 to 1% of the material thickness when installed is provided on the bonding surface. For example, when manufacturing a clad steel plate from a 100 mm thick slab, plating is performed to a thickness of 200 to 1000 μm or Ni foil is charged.
Ni膜の厚さを接合時の材料厚さの02%以上の厚さに
限定しtコのは、02%未満では、後記の本発明の製造
条件と組み合せても炭素の拡散移動を完全に防止できな
いのと、例えば層下に仕上げた時に接合境界が鮮明でな
く商品価値が低下するからである。また、1%を越える
と芯材と合せ材の接着不良が生じやすくなるからである
。The thickness of the Ni film is limited to 0.2% or more of the material thickness at the time of bonding.If it is less than 0.2%, carbon diffusion and movement cannot be completely prevented even when combined with the manufacturing conditions of the present invention described later. This is because it cannot be prevented and, for example, when finishing under a layer, the bonding boundary is not clear and the commercial value decreases. Moreover, if it exceeds 1%, poor adhesion between the core material and the laminate material tends to occur.
Ni膜厚を薄くできろことは大型鋼塊または大型スラブ
から製造する場合に極めて有利である。Being able to reduce the Ni film thickness is extremely advantageous when manufacturing from large steel ingots or large slabs.
すなわち、接合面積が大きくなると一定膜厚のものを製
造しがたく、局部的に膜厚が厚くなったところは接着不
良を生じる場合があるからである。That is, if the bonding area becomes large, it is difficult to manufacture a film with a constant thickness, and a locally thick film may lead to poor adhesion.
次に熱間圧延において600〜500℃の温度範囲で鋼
帯を巻取るが、この巻取温度の管理は接合面に設けられ
たN1膜の炭素拡散防止作用と冷延時の圧下率が大きく
なった場合の芯材の亀裂防止から設定される。Next, the steel strip is wound in a temperature range of 600 to 500°C during hot rolling, but the control of this winding temperature is due to the carbon diffusion prevention effect of the N1 film provided on the joint surface and the large reduction rate during cold rolling. It is set to prevent cracks in the core material when
熱延鋼帯の巻取温度および冷間圧延率を種々変更して芯
材に亀裂を生じる冷間圧延率を調査し、その結果を第2
図に示した。第2図における各表示の条件は次のとおり
である。The coiling temperature and cold rolling rate of the hot rolled steel strip were varied to investigate the cold rolling rate that caused cracks in the core material, and the results were used in the second study.
Shown in the figure. The conditions for each display in FIG. 2 are as follows.
O印:熱延鋼帯の熱処理(750℃×1分)を行った時
の芯材に亀裂を生じ始める冷間圧延率、ただし、接合部
の高炭素鋼の脱炭なし。O mark: Cold rolling rate at which cracks begin to occur in the core material when the hot rolled steel strip is heat treated (750°C x 1 minute), but there is no decarburization of the high carbon steel at the joint.
・印:熱延鋼帯の熱処理(750℃×1分)を行った時
の芯材に亀裂を生し始める冷間圧延率、ただし、接合部
の高炭素≦4の脱炭あり。・Mark: Cold rolling rate at which cracks begin to form in the core material when hot-rolled steel strip is heat treated (750°C x 1 minute), but there is decarburization with high carbon ≦4 at the joint.
×印:熱延鍔帯の熱処理なしのとき芯材に亀裂を生じる
冷間圧延率。×: Cold rolling rate that causes cracks in the core material when the hot-rolled collar is not heat-treated.
芯材から合せ材への炭素の拡散を防止するにはNi1f
iの厚みが大きいほど効果的であるが、熱延の巻取温度
が600℃を越丸ると接合面のNi膜の厚さが材料厚さ
の2%程度であっても、第2図に示す如く炭素の拡散移
動を防止することができないので、上限を600℃とし
た。To prevent carbon diffusion from the core material to the cladding material, use Ni1f.
The larger the thickness of i, the more effective it is, but if the hot-rolling temperature exceeds 600°C, even if the thickness of the Ni film on the joint surface is about 2% of the material thickness, as shown in Figure 2. As shown in the figure, since the diffusion and movement of carbon cannot be prevented, the upper limit was set at 600°C.
熱延巻取温度が500℃未満では、熱延鋼帯の熱処理を
行っても軟化が十分でなく、第2図に示す如く、冷延率
が30%程度で高炭素鋼の亀裂を生じるので、下限を5
00℃とした。If the hot-rolling coiling temperature is less than 500°C, even if the hot-rolled steel strip is heat-treated, the softening will not be sufficient, and as shown in Figure 2, cracks will occur in the high carbon steel at a cold rolling reduction of about 30%. , set the lower limit to 5
The temperature was 00°C.
次に冷間圧延前の熱延鋼帯の熱処理であるが、加熱温度
と保持時間の関係を第1図に示した。第1図において各
表示の条件は次のとおりである。Next, regarding the heat treatment of the hot rolled steel strip before cold rolling, the relationship between heating temperature and holding time is shown in FIG. The conditions for each display in FIG. 1 are as follows.
O印:冷間圧延率70%までは芯材の亀裂がなく、接合
部の脱炭もない。O mark: No cracks in the core material and no decarburization at the joints up to a cold rolling rate of 70%.
×印:冷延での芯材の亀裂はないが、接合部に脱炭を生
じる。× mark: There is no crack in the core material during cold rolling, but decarburization occurs at the joint.
Δ印:冷間圧延が30〜40%になると芯材に亀裂を生
じるが、接合部の脱炭はない。Δ mark: When cold rolling reaches 30 to 40%, cracks occur in the core material, but there is no decarburization at the joint.
本発明においては、第1図の結果から、冷間圧延前の熱
延鋼帯に第1図の座標A、B、、C,D。In the present invention, from the results shown in FIG. 1, the coordinates A, B, , C, and D in FIG. 1 are applied to the hot rolled steel strip before cold rolling.
E、F、G、Hで囲まれる斜線で示した範囲内の加熱温
度と保持時間の熱処理を実施する。なお、各座標の値は
次の如くである。Heat treatment is performed at a heating temperature and holding time within the shaded range surrounded by E, F, G, and H. Note that the values of each coordinate are as follows.
座標 加熱温度(’C) 保持時間(分)A
700 3B
750 2C7501
D 800 1E
850 1F 800
2G 800
3H7503
第1図から熱処理の加熱温度および保持時間が下限を外
れろと、熱延鋼帯の芯材の軟化が不十分で冷延率が高く
なると芯材に亀裂を生じ、加熱温度および保持時間の上
限を外れると接合面において炭素の拡散移動が生じるこ
とがわかる。よって本発明においては、加熱温度および
保持時間を第1図における座標A、B、C,D、E、F
、、G。Coordinates Heating temperature ('C) Holding time (minutes) A
700 3B
750 2C7501 D 800 1E
850 1F 800
2G 800
3H7503 Figure 1 shows that if the heating temperature and holding time of heat treatment are outside the lower limit, if the core material of the hot rolled steel strip is not sufficiently softened and the cold rolling rate is high, cracks will occur in the core material. It can be seen that when the upper limit of is exceeded, diffusion and movement of carbon occurs at the bonding surface. Therefore, in the present invention, the heating temperature and holding time are adjusted to the coordinates A, B, C, D, E, F in FIG.
,,G.
Hに囲まれる範囲内に限定した。It was limited to the range surrounded by H.
また、加熱温度、保持時間および冷延時芯材に亀裂を生
じ始める冷間圧延率との関係を第3図に示した。Further, FIG. 3 shows the relationship among heating temperature, holding time, and cold rolling rate at which cracks begin to appear in the core material during cold rolling.
本発明は上記の如く接合面のNi膜の厚さ、熱延時の鋼
帯巻取温度および熱延鋼帯の熱処理の3者を適正な条件
で組合せることによって、接合面における炭素の拡散移
動を防止し、冷延におけろ芯材の亀裂を防止することが
できる。As described above, the present invention achieves carbon diffusion movement on the joint surface by combining the thickness of the Ni film on the joint surface, the coiling temperature of the steel strip during hot rolling, and the heat treatment of the hot rolled steel strip under appropriate conditions. This can prevent cracks in the core material during cold rolling.
なお、従来の高炭素鋼の均一微細化を図ることを目的と
するAc、変態点直下の温度に長時間保持し、 Ac、
変態点もしくはAc、変態点直上の温度に加熱した後徐
冷する熱処理方法あるいはみがき特殊帯鋼の連続炉にお
ける焼入れ、焼戻し方法等はいずれも本発明とその目的
、構成1作用を異にしている。In addition, Ac, which aims to achieve uniform refinement of conventional high carbon steel, is maintained at a temperature just below the transformation point for a long time,
The transformation point or Ac, a heat treatment method of heating to a temperature just above the transformation point and then slow cooling, or a method of quenching and tempering polished special strip steel in a continuous furnace, etc., are all different from the present invention in their purpose and configuration 1 operation. .
炭緊工具鋼j]材SK3を芯材、ステンレスmSO34
10を合せ材として、クラツド比35%の厚み100
mmの3層クラッドスラブを製造した。Charcoal tension tool steel j] material SK3 as core material, stainless steel mSO34
10 as a laminating material, thickness 100 with a cladding ratio of 35%
A three-layer clad slab of mm was produced.
)″A素工具S1泪材と接するステンンス鍔の表面に2
00μm厚のN1めっきを行った後3 、gクラッドに
組立てた。組立てスラブを1200℃に加熱後3關厚の
鋼帯に熱延し600〜509℃の温度でコイルに巻取っ
た。次にこの熱延鋼帯を連続焼純酸洗ラインにおいて8
00℃×2分の熱処理、ショットピーニングおよび酸洗
を行い、続いて1關厚に冷間圧延を行った。この本発明
実施例のクラッド冷延鋼板について調査した結果、接合
面の芯材に脱炭はなく、また、芯材の亀裂のないことが
確認された。)'' A raw tool S1 2 on the surface of the stainless steel tsuba in contact with the material
After performing N1 plating with a thickness of 00 μm, it was assembled into a G cladding. The assembled slab was heated to 1200°C, then hot rolled into a 3-inch thick steel strip and wound into a coil at a temperature of 600-509°C. Next, this hot-rolled steel strip is passed through a continuous annealing pickling line.
Heat treatment at 00° C. for 2 minutes, shot peening and pickling were performed, followed by cold rolling to one thickness. As a result of investigating the clad cold-rolled steel sheet of this example of the present invention, it was confirmed that there was no decarburization in the core material at the joint surface and that there were no cracks in the core material.
一方、比較のため同種の3層クラッドスラブを同じ条件
で熱延し750〜650℃の温度でコイルに巻取り、熱
延鋼帯を熱処理することな(3mmから1 mmに冷延
したものは芯材の亀裂発生はなかったが、接合面におい
て炭素の拡散移動を生じていた。また、熱延鋼帯を60
0〜500℃で巻取り、更に850℃×3分の熱処理を
行った後3胴から11TIff+に冷間圧延した場合に
おし)でも、同様に芯材に亀裂は発生しなかったが接合
面に8いて炭素の拡散移動が行われてし)な。On the other hand, for comparison, a three-layer clad slab of the same type was hot-rolled under the same conditions and wound into a coil at a temperature of 750 to 650°C. Although there were no cracks in the core material, carbon diffusion and movement occurred at the joint surface.
Similarly, no cracks occurred in the core material, but the joint surface 8, carbon diffusion and movement took place).
本発明は上記実施例からも明らかな如く、3層のステン
レスクラッド鋼の製造に際し、接合面に材料厚さの02
〜1%の厚さのNi膜を設け、熱間圧延で600〜50
0℃の温度範囲でコイルを巻取り、その後、限定条件の
熱処理を行い、接合面の炭素の拡散移動と冷延時の芯材
の亀裂発生を防止することによって、従来に比して著し
くコストを低減し、また、大型の鋼塊やスラブからステ
ンレスクラッド鋼の製造を可能とした。As is clear from the above embodiments, the present invention has a material thickness of 0.2 mm on the joint surface when manufacturing three-layer stainless clad steel.
A Ni film with a thickness of ~1% is provided, and the thickness is 600 ~ 50 by hot rolling.
By winding the coil in a temperature range of 0°C and then performing heat treatment under limited conditions to prevent the diffusion of carbon on the bonding surface and the occurrence of cracks in the core material during cold rolling, costs are significantly reduced compared to conventional methods. It also made it possible to manufacture stainless clad steel from large steel ingots and slabs.
第1図は熱延鋼帯の熱処理における加熱:」度および保
持時間と冷延鋼帯の芯材の亀裂および接合部の脱炭の有
無との関係を示す関係図、第2図は熱延の巻取温度と冷
延における芯材に亀裂を生じる冷間圧延率との関係を示
す関係図、第3図は熱延鋼帯の熱処理の加熱温度および
保持時間と冷延時芯材に亀裂を生じ始める冷間圧延率と
の関係を示す線図である。Figure 1 is a relationship diagram showing the relationship between the heating degree and holding time during heat treatment of hot-rolled steel strips and cracks in the core material of cold-rolled steel strips and the presence or absence of decarburization at joints. Figure 3 shows the relationship between the coiling temperature and the cold rolling rate that causes cracks in the core material during cold rolling. FIG. 3 is a diagram showing the relationship with the cold rolling reduction that starts to occur.
Claims (1)
ステンレス鋼とする3層のステンレスクラッド鋼の製造
方法において、接合面に接合後の材料厚さの0.2〜1
%の厚さのNi膜を設ける工程と、コイル巻取温度を6
00〜500℃の温度範囲とする熱間圧延工程と、冷間
圧延前に加熱温度および保持時間をそれぞれ座標軸とす
る図面の下記座標A、B、C、D、E、F、G、Hで囲
まれる範囲内の加熱温度と保持時間で熱延鋼帯を熱処理
する工程と、を有して成ることを特徴とするステンレス
クラッド鋼の製造方法。 記 座標 加熱温度(℃) 保持時間(分) A 700 3 B 750 2 C 750 1 D 800 1 E 850 1 F 800 2 G 800 3 H 750 3(1) In a method for manufacturing three-layer stainless clad steel in which the core material is carbon tool steel SK1 to SK5 and the mating material is stainless steel, the thickness of the material after joining is 0.2 to 1
The process of providing a Ni film with a thickness of 6% and the coil winding temperature of 6%.
The following coordinates A, B, C, D, E, F, G, H in the drawing with the coordinate axes of the hot rolling process with a temperature range of 00 to 500 ° C, and the heating temperature and holding time before cold rolling, respectively. A method for producing stainless clad steel, comprising the steps of: heat-treating a hot-rolled steel strip at a heating temperature and holding time within the enclosed range. Coordinates Heating temperature (℃) Holding time (minutes) A 700 3 B 750 2 C 750 1 D 800 1 E 850 1 F 800 2 G 800 3 H 750 3
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP23293486A JPH07100825B2 (en) | 1986-09-30 | 1986-09-30 | Manufacturing method of stainless clad steel |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP23293486A JPH07100825B2 (en) | 1986-09-30 | 1986-09-30 | Manufacturing method of stainless clad steel |
Publications (2)
Publication Number | Publication Date |
---|---|
JPS6386817A true JPS6386817A (en) | 1988-04-18 |
JPH07100825B2 JPH07100825B2 (en) | 1995-11-01 |
Family
ID=16947139
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
JP23293486A Expired - Fee Related JPH07100825B2 (en) | 1986-09-30 | 1986-09-30 | Manufacturing method of stainless clad steel |
Country Status (1)
Country | Link |
---|---|
JP (1) | JPH07100825B2 (en) |
Cited By (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
WO2002103073A3 (en) * | 2001-06-15 | 2004-05-21 | Nippon Steel Corp | High-strength alloyed aluminum-system plated steel sheet and high-strength automotive part excellent in heat resistance and after-painting corrosion resistance |
JP2013209688A (en) * | 2012-03-30 | 2013-10-10 | Nippon Steel & Sumikin Stainless Steel Corp | Clad steel sheet having duplex stainless steel as mating material, and method for producing the same |
CN111941003A (en) * | 2020-07-15 | 2020-11-17 | 昆明理工大学 | Preparation method of warm-rolled stainless steel/carbon steel composite plate |
-
1986
- 1986-09-30 JP JP23293486A patent/JPH07100825B2/en not_active Expired - Fee Related
Cited By (4)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
WO2002103073A3 (en) * | 2001-06-15 | 2004-05-21 | Nippon Steel Corp | High-strength alloyed aluminum-system plated steel sheet and high-strength automotive part excellent in heat resistance and after-painting corrosion resistance |
CN100370054C (en) * | 2001-06-15 | 2008-02-20 | 新日本制铁株式会社 | High-strength alloyed aluminum-system plated steel sheet and high-strength automotive part excellent in heat resistance and after-painting corrosion resistance |
JP2013209688A (en) * | 2012-03-30 | 2013-10-10 | Nippon Steel & Sumikin Stainless Steel Corp | Clad steel sheet having duplex stainless steel as mating material, and method for producing the same |
CN111941003A (en) * | 2020-07-15 | 2020-11-17 | 昆明理工大学 | Preparation method of warm-rolled stainless steel/carbon steel composite plate |
Also Published As
Publication number | Publication date |
---|---|
JPH07100825B2 (en) | 1995-11-01 |
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LAPS | Cancellation because of no payment of annual fees |