JPH03229819A - Production of clad steel plate excellent in corrosion resistance - Google Patents
Production of clad steel plate excellent in corrosion resistanceInfo
- Publication number
- JPH03229819A JPH03229819A JP2207590A JP2207590A JPH03229819A JP H03229819 A JPH03229819 A JP H03229819A JP 2207590 A JP2207590 A JP 2207590A JP 2207590 A JP2207590 A JP 2207590A JP H03229819 A JPH03229819 A JP H03229819A
- Authority
- JP
- Japan
- Prior art keywords
- corrosion resistance
- steel
- steel plate
- cast slab
- alloy 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.)
- Pending
Links
- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 44
- 239000010959 steel Substances 0.000 title claims abstract description 44
- 230000007797 corrosion Effects 0.000 title claims abstract description 22
- 238000005260 corrosion Methods 0.000 title claims abstract description 22
- 238000004519 manufacturing process Methods 0.000 title claims description 24
- 229910000851 Alloy steel Inorganic materials 0.000 claims abstract description 19
- 238000001816 cooling Methods 0.000 claims abstract description 14
- 239000002344 surface layer Substances 0.000 claims abstract description 11
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims abstract description 6
- 238000005098 hot rolling Methods 0.000 claims abstract description 5
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 5
- 229910052757 nitrogen Inorganic materials 0.000 claims abstract description 5
- 229910052758 niobium Inorganic materials 0.000 claims abstract description 3
- 239000002131 composite material Substances 0.000 claims description 16
- 238000000034 method Methods 0.000 claims description 15
- 238000009749 continuous casting Methods 0.000 claims description 9
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 8
- 239000012535 impurity Substances 0.000 claims description 5
- 229910052802 copper Inorganic materials 0.000 claims description 4
- 229910052742 iron Inorganic materials 0.000 claims description 4
- 229910052759 nickel Inorganic materials 0.000 claims description 3
- 229910052750 molybdenum Inorganic materials 0.000 claims description 2
- 229910052720 vanadium Inorganic materials 0.000 claims description 2
- 239000010410 layer Substances 0.000 abstract description 13
- 238000010438 heat treatment Methods 0.000 abstract description 6
- 238000005266 casting Methods 0.000 abstract description 3
- 229910052719 titanium Inorganic materials 0.000 abstract description 2
- 239000000203 mixture Substances 0.000 abstract 2
- 239000000853 adhesive Substances 0.000 abstract 1
- 230000001070 adhesive effect Effects 0.000 abstract 1
- 239000000463 material Substances 0.000 description 16
- 230000000694 effects Effects 0.000 description 9
- 238000005096 rolling process Methods 0.000 description 7
- 239000010949 copper Substances 0.000 description 5
- 239000010936 titanium Substances 0.000 description 5
- 229910001566 austenite Inorganic materials 0.000 description 4
- 239000002648 laminated material Substances 0.000 description 4
- 229910001220 stainless steel Inorganic materials 0.000 description 4
- 229910052717 sulfur Inorganic materials 0.000 description 3
- 230000007704 transition Effects 0.000 description 3
- CURLTUGMZLYLDI-UHFFFAOYSA-N Carbon dioxide Chemical compound O=C=O CURLTUGMZLYLDI-UHFFFAOYSA-N 0.000 description 2
- 229910000532 Deoxidized steel Inorganic materials 0.000 description 2
- 229910045601 alloy Inorganic materials 0.000 description 2
- 239000000956 alloy Substances 0.000 description 2
- 239000010953 base metal Substances 0.000 description 2
- 230000000052 comparative effect Effects 0.000 description 2
- 230000006866 deterioration Effects 0.000 description 2
- 238000004880 explosion Methods 0.000 description 2
- 238000010030 laminating Methods 0.000 description 2
- 229910052751 metal Inorganic materials 0.000 description 2
- 239000002184 metal Substances 0.000 description 2
- VNWKTOKETHGBQD-UHFFFAOYSA-N methane Chemical compound C VNWKTOKETHGBQD-UHFFFAOYSA-N 0.000 description 2
- 229910052698 phosphorus Inorganic materials 0.000 description 2
- 238000001556 precipitation Methods 0.000 description 2
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 1
- 229910000570 Cupronickel Inorganic materials 0.000 description 1
- RWSOTUBLDIXVET-UHFFFAOYSA-N Dihydrogen sulfide Chemical compound S RWSOTUBLDIXVET-UHFFFAOYSA-N 0.000 description 1
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 1
- 230000002411 adverse Effects 0.000 description 1
- 238000005452 bending Methods 0.000 description 1
- 229910002092 carbon dioxide Inorganic materials 0.000 description 1
- 239000001569 carbon dioxide Substances 0.000 description 1
- 230000003749 cleanliness Effects 0.000 description 1
- 238000009792 diffusion process Methods 0.000 description 1
- 239000012530 fluid Substances 0.000 description 1
- 239000007789 gas Substances 0.000 description 1
- 229910000037 hydrogen sulfide Inorganic materials 0.000 description 1
- 229910001293 incoloy Inorganic materials 0.000 description 1
- 229910001026 inconel Inorganic materials 0.000 description 1
- 229910000734 martensite Inorganic materials 0.000 description 1
- 150000002739 metals Chemical class 0.000 description 1
- 239000003345 natural gas Substances 0.000 description 1
- 230000003647 oxidation Effects 0.000 description 1
- 238000007254 oxidation reaction Methods 0.000 description 1
- 239000011120 plywood Substances 0.000 description 1
- 238000005498 polishing Methods 0.000 description 1
- 238000002360 preparation method Methods 0.000 description 1
- 238000007670 refining Methods 0.000 description 1
- 239000010935 stainless steel Substances 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
- 238000009864 tensile test Methods 0.000 description 1
- 238000007751 thermal spraying Methods 0.000 description 1
- 150000003568 thioethers Chemical class 0.000 description 1
- 238000003466 welding Methods 0.000 description 1
- 229910000859 α-Fe Inorganic materials 0.000 description 1
Abstract
Description
【発明の詳細な説明】
(産業上の利用分野)
本発明は耐食性に優れた複合鋼板の製造方法に関し、特
に、表層部が高合金鋼、内部が普通鋼あるいは低合金鋼
からなる耐食性に優れた複合鋼板の製造方法に関するも
のである。[Detailed Description of the Invention] (Industrial Application Field) The present invention relates to a method of manufacturing a composite steel plate with excellent corrosion resistance, and in particular, to a method of manufacturing a composite steel plate with excellent corrosion resistance, in which the surface layer is made of high alloy steel and the inner part is made of ordinary steel or low alloy steel. The present invention relates to a method for manufacturing composite steel sheets.
(従来の技術)
石油や天然ガス用輸送管の使用条件は、近年益々過酷に
なりつつある。例えば、硫化水素や炭酸ガスを多く含み
、しかもpH的にも厳しい流体をラインパイプによって
輸送する場合、操業上の安定性、安全性等の面から、こ
のような使用条件に十分耐える耐食性、靭性、強度、そ
の他のラインパイプ用輸送鋼管として具備すべき特性を
兼ね備えた鋼管に対する要望が高まっている。(Prior Art) The operating conditions for oil and natural gas transport pipes have become increasingly severe in recent years. For example, when transporting fluids that contain large amounts of hydrogen sulfide and carbon dioxide gas and have a harsh pH, line pipes must have sufficient corrosion resistance and toughness to withstand such usage conditions in terms of operational stability and safety. There is an increasing demand for steel pipes that have the characteristics required for transportation steel pipes for line pipes, such as steel pipes, strength, and other properties.
このような要望から、パイプラインの材料は、従来から
用いられた普通鋼や低合金鋼の代わりに高合金鋼を用い
る傾向にあるが、高合金鋼のみで鋼管を製造すると経済
的に不利となる。Due to these demands, there is a tendency to use high-alloy steel instead of the conventionally used ordinary steel or low-alloy steel, but manufacturing steel pipes only from high-alloy steel is economically disadvantageous. Become.
そこで、比較的に安価な普通鋼や低合金鋼を母材とし、
高価なステンレス鋼等の高耐食性高含金銅を合わせ材と
するクラツド鋼管が開発され、使用されている。Therefore, we decided to use relatively inexpensive ordinary steel or low alloy steel as the base material.
Clad steel pipes made of expensive stainless steel or other highly corrosion-resistant, high-metallic copper have been developed and are now in use.
このようなりラッド鋼管の製造法には、特公昭64−7
138号公報に示すような圧延法、爆着法、鋳込法、拡
散法および溶射法等がある。例えば、圧延法においては
母材と合わせ材との密着性を確保するために、密着面の
表面研磨、さらには加熱・圧延時における酸化を防止す
るための4周溶接並びに真空引き等の配慮がスラブ組立
時に必要である。This method of manufacturing rad steel pipes was developed in the 1980s.
There are rolling methods, explosion bonding methods, casting methods, diffusion methods, thermal spraying methods, etc. as shown in Japanese Patent No. 138. For example, in the rolling method, in order to ensure adhesion between the base material and the composite material, considerations such as surface polishing of the adhesion surface, four-circle welding and vacuuming to prevent oxidation during heating and rolling are required. Necessary when assembling slabs.
しかしながら、これらの作業はコスト面に問題があり、
また、密着面全体の密着性の確保に問題があった。However, these operations have cost problems,
In addition, there was a problem in ensuring adhesion of the entire contact surface.
爆着法、鋳込法等のその他の製造法においても、同様の
問題があり、製造コストの低減並びに母材と合わせ材と
の密着性の安定的な確保が、複合鋼板製造上の大きな問
題となっていた。Similar problems exist in other manufacturing methods such as the explosion bonding method and the casting method, and reducing manufacturing costs and ensuring stable adhesion between the base material and the composite material are major issues in manufacturing composite steel sheets. It became.
また、最近は連続鋳造法で表層部と内部がそれぞれ異な
る金属から構成される複層鋳片を製造する方法が、例え
ば特開昭83−108947号公報等で提示されている
。Recently, a method of manufacturing a multi-layer slab whose surface layer and interior are made of different metals using a continuous casting method has been proposed, for example, in Japanese Patent Application Laid-Open No. 83-108947.
(発明が解決しようとする課題)
本発明者等は連続鋳造法により複層鋳片を製造し、これ
を圧延成形することにより耐食性の優れた複合鋼板を製
造することを工夫し、クラツド鋼板として母材と合わせ
材の密着性に優れるばかりか、耐食性に優れて、且つこ
のクラツド鋼板を鋼管等に加工成形できることを見出し
た。(Problems to be Solved by the Invention) The present inventors have devised a method of manufacturing a composite steel plate with excellent corrosion resistance by manufacturing a multi-layer slab using a continuous casting method and rolling forming the same. It has been discovered that this clad steel plate not only has excellent adhesion between the base material and the laminated material, but also has excellent corrosion resistance, and can be processed and formed into steel pipes and the like.
(課題を解決するための手段)
本発明の要旨とするところは、表層部が高合金鋼、内部
が重量%でC:0.06%以下、S j:0.80%以
下、Mn : 0.8(1〜1.50%、Nb : [
1,005〜0.05%、A、77:0.06%以下、
T i : 0.005〜0.03%、N:0.005
%以下、残部が鉄および不可避不純物からなる複層鋳片
を連続鋳造で製造し、該鋳片を1100〜1300℃に
加熱し、次いで熱間圧延を仕上温度650℃以上で行っ
た後、空冷または水冷することを特徴とする耐食性に優
れた複合鋼板の製造方法および連続鋳造で、表層部が高
合金鋼、内部が重量%でc : o、oe%以下、s
i:0.80%以下、Mn:0.80〜1.50%、N
b:0.005〜0.05%、AI:0.06%以下、
Tに〇、005〜0.03%、N :0.005%以下
さらに、Ca:0.001〜0.006%、Cu:0.
05〜0.5%、N i : 0.1)5〜0.5%、
V : 0.(II−0.10%、Mo:0.05〜0
.30%の1種または2種以上を更に含有し、残部が鉄
および不可避不純物からなる複層鋳片を製造し、該鋳片
を1100〜1300℃に加熱し、次いで熱間圧延を仕
上温度650℃以上で行った後、空冷または水冷するこ
とを特徴とする耐食性に優れた複合鋼板の製造方法であ
る。(Means for Solving the Problems) The gist of the present invention is that the surface layer is made of high alloy steel, the inside is made of C: 0.06% or less, S j: 0.80% or less, Mn: 0. .8 (1-1.50%, Nb: [
1,005 to 0.05%, A, 77: 0.06% or less,
Ti: 0.005-0.03%, N: 0.005
% or less, the balance being iron and unavoidable impurities, is produced by continuous casting. The slab is heated to 1100 to 1300°C, then hot rolled at a finishing temperature of 650°C or higher, and then air cooled. Or, a method for manufacturing a composite steel plate with excellent corrosion resistance characterized by water cooling and continuous casting, in which the surface layer is made of high-alloy steel and the interior is made of high-alloy steel and the inside is made of c: o, oe% or less, s.
i: 0.80% or less, Mn: 0.80 to 1.50%, N
b: 0.005 to 0.05%, AI: 0.06% or less,
T: 005-0.03%, N: 0.005% or less, Ca: 0.001-0.006%, Cu: 0.
05-0.5%, Ni: 0.1) 5-0.5%,
V: 0. (II-0.10%, Mo: 0.05-0
.. A multi-layer slab containing 30% of one or more of the above and the remainder consisting of iron and unavoidable impurities is produced, the slab is heated to 1100-1300°C, and then hot rolled at a finishing temperature of 650°C. This is a method for producing a composite steel sheet with excellent corrosion resistance, which is characterized by carrying out the process at a temperature of 0.degree. C. or higher, followed by air cooling or water cooling.
(作 用) 以下、本発明について説明する。(for production) The present invention will be explained below.
(1)合わせ材(表層材)
合わせ材としては、耐食性に優れた高合金鋼成分を採用
する。ここで言う、耐食性に優れた高合金鋼とは、オー
ステナイト系ステンレス鋼、2相系ステンレス鋼等のス
テンレス鋼は勿論インコロイまたはインコネル等の高N
i高合金鋼、チタンあるいはキュプロニッケル等の耐食
性に優れた金属または合金を意味し、その選択は使用環
境に応じて決定されるべきものである。(1) Laminating material (surface layer material) As the laminating material, a high alloy steel component with excellent corrosion resistance is used. High alloy steels with excellent corrosion resistance include stainless steels such as austenitic stainless steels and duplex stainless steels, as well as high N steels such as Incoloy and Inconel.
i means a metal or alloy with excellent corrosion resistance such as high alloy steel, titanium, or cupronickel, and the selection should be determined depending on the usage environment.
(2)母材(内層材)
C:内層材のC量は連続鋳造による複合鋼板の製造にお
いて最も重要な意味を持つ。すなわち、連続鋳造にて複
層鋳片を製造する際、表層部と内層部との界面には不可
避的に、遷移層が生じる。表層部に高合金鋼成分を採用
した場合、内部の母材成分中のC量が高いと、この遷移
層にマルテンサイトが生じやすく、内部割れが生じるこ
とが筆者らの研究により明らかになった。(2) Base material (inner layer material) C: The amount of C in the inner layer material has the most important meaning in the production of composite steel sheets by continuous casting. That is, when manufacturing a multilayer slab by continuous casting, a transition layer is inevitably generated at the interface between the surface layer and the inner layer. The authors' research has revealed that when high-alloy steel components are used in the surface layer, if the C content in the internal base material component is high, martensite is likely to form in this transition layer, causing internal cracks. .
すなわち、C量が0.06%を超えると遷移層の内部割
れが顕著になることから、その上限を0.06%とする
必要がある。なお、合わせ材のC量に応じて母材のC量
は合わせ材のC量以下とすることが望ましい。That is, if the C content exceeds 0.06%, internal cracks in the transition layer become noticeable, so the upper limit needs to be set to 0.06%. Note that, depending on the amount of C in the laminated material, it is desirable that the amount of C in the base material is equal to or less than the amount of C in the laminated material.
Si:Siは脱酸上鋼に含まれる元素であるか、その過
剰添加は溶接性、HAZ靭性を阻害する。Si: Si is an element contained in deoxidized steel, and its excessive addition inhibits weldability and HAZ toughness.
従って、その上限を0.8%とする。Therefore, the upper limit is set at 0.8%.
Mn:Mnは、強度、靭性並びに焼入性を確保する上で
有用な元素であり、0.8%以上の添加か必要である。Mn: Mn is a useful element for ensuring strength, toughness, and hardenability, and must be added in an amount of 0.8% or more.
しかし、Mnff1が多すぎると溶接性、HAZ靭性の
劣化を招くためその上限を1.5%とした。However, too much Mnff1 causes deterioration of weldability and HAZ toughness, so the upper limit was set at 1.5%.
Nb:下限を0.005%としたのは、Nbの析出効果
により強度を得るためである。また、溶体化温度に加熱
した際に、オーステナイト粒の粗大化の防止作用、すな
わち、Nb(CN)として母材に微細に均一分散させる
作用を有する。Nb: The reason why the lower limit is set to 0.005% is to obtain strength through the precipitation effect of Nb. Furthermore, when heated to the solution temperature, it has the effect of preventing coarsening of austenite grains, that is, the effect of finely and uniformly dispersing Nb (CN) in the base material.
一方、0.05%以上になると靭性か劣化する。On the other hand, if it exceeds 0.05%, the toughness deteriorates.
従って、その上限を0.05%とした。Therefore, the upper limit was set at 0.05%.
Al:A、Qは一般に脱酸上鋼に含まれる元素であるが
、SiおよびMnあるいはTiによっても脱酸は行われ
るので、本発明ではAlについては下限を限定しない。Al: A and Q are generally elements contained in deoxidized steel, but since deoxidation is also performed by Si, Mn, or Ti, the present invention does not limit the lower limit of Al.
しかし、ANfflか多くなると鋼の清浄度が悪くなり
、HAZ靭性が劣化するので上限を0.06%とした。However, if ANffl increases, the cleanliness of the steel deteriorates and the HAZ toughness deteriorates, so the upper limit was set at 0.06%.
Ti:Tiはオーステナイト粒の細粒化に有効であり、
靭性確保の観点から0.005%以上の添加が必要であ
る。一方、0.03%を超えると、溶接性の劣化を招き
、好ましくないため、上限を0.03%とした。Ti: Ti is effective in refining austenite grains,
From the viewpoint of ensuring toughness, it is necessary to add 0.005% or more. On the other hand, if it exceeds 0.03%, it causes deterioration of weldability, which is not preferable, so the upper limit was set at 0.03%.
N:Nは溶鋼中に不可避的に混入し鋼の靭性を劣化させ
るために、その上限を0.005%とした。N: Since N inevitably mixes into molten steel and deteriorates the toughness of the steel, its upper limit was set at 0.005%.
P、S:P、Sは不可避的不純物として鋼中に含まれる
。本発明ではその上限を敢えて限定しないが、これらは
母材並びに溶接部の靭性を劣化させるため、その量は極
力少なくすることが好ましい。P, S: P and S are contained in steel as inevitable impurities. In the present invention, the upper limit is not intentionally limited, but since these deteriorate the toughness of the base metal and the welded part, it is preferable to reduce the amount as much as possible.
本発明鋼においては、さらに必要によりCa:0.00
1〜0.006%、Cu:0.05〜0.5%、Ni:
0.05〜05%、V : 0.01〜0.10%、M
o+0.05〜0.30%のうちいずれか1種または2
種以上を含有させる。In the steel of the present invention, if necessary, Ca: 0.00
1-0.006%, Cu: 0.05-0.5%, Ni:
0.05-05%, V: 0.01-0.10%, M
o + Any one or two of 0.05 to 0.30%
Contain more than seeds.
これらの元素を添加する主たる目的は、本発明鋼の優れ
た特徴を損なうことなく強度、靭性など諸特性の向上を
はかるためである。したがってその添加量は自ら制限さ
れるべき性質のものである。The main purpose of adding these elements is to improve various properties such as strength and toughness without impairing the excellent characteristics of the steel of the present invention. Therefore, the amount added must be limited.
Ca:Caは硫化物の形態を制御し、シャルピー吸収エ
ネルギーを増加させ低温靭性を向上させる。しかし、C
a量は0.001%未満では実用上効果がなく、また、
o、ooe%を超えるとCaS、CaO等の大型介在物
を生じるため、その上限を0.006%とした。Ca: Ca controls the morphology of sulfides, increases Charpy absorbed energy, and improves low temperature toughness. However, C
If the amount of a is less than 0.001%, there is no practical effect, and
If it exceeds o, ooe%, large inclusions such as CaS and CaO occur, so the upper limit was set at 0.006%.
Nj:NiはHAZ硬化性および靭性に悪影響を与える
ことなく母材の強度、靭性を向上させる特性を持ち、0
.05%以上の添加が必要である。Nj: Ni has the property of improving the strength and toughness of the base material without adversely affecting HAZ hardenability and toughness, and
.. It is necessary to add 0.05% or more.
また、0.5%を超えるとHAZの硬化性および靭性上
好ましくないため、上限を0.5%とした。In addition, if it exceeds 0.5%, it is unfavorable in terms of hardenability and toughness of the HAZ, so the upper limit was set to 0.5%.
Cu: CuはNiとほぼ同様の効果を持ち、0.05
%上の添加が必要である。しかし、0.5%を超えると
熱間加工性が劣化するため、その上限を0.5%とした
。Cu: Cu has almost the same effect as Ni, 0.05
% addition is necessary. However, if it exceeds 0.5%, hot workability deteriorates, so the upper limit was set at 0.5%.
V=Vは析出効果に有効であるが、0.01%以上添加
しないとその効果がない。また、0.10%を超えると
溶接性の劣化を招き好ましくないため、その上限を0.
10%とした。Although V=V is effective for the precipitation effect, it has no effect unless it is added in an amount of 0.01% or more. Moreover, if it exceeds 0.10%, weldability deteriorates, which is undesirable, so the upper limit should be set at 0.10%.
It was set at 10%.
M o : M oは母材の強度、靭性を共に向上させ
る元素であるが、0.05%以上添加しないとその効果
がない。また、0.30%を超えると溶接部靭性および
溶接性の劣化を招き好ましくないため、上限を0.30
%とした。Mo: Mo is an element that improves both the strength and toughness of the base material, but it has no effect unless it is added in an amount of 0.05% or more. In addition, if it exceeds 0.30%, the weld toughness and weldability will deteriorate, which is undesirable, so the upper limit should be set at 0.30%.
%.
(3)製造方法
連続鋳造により複層鋳片を製造し、該鋳片に熱間圧延を
施すため従来の大型鋼板の製造方法とプロセス的には相
違がなく、クラッド鋼板製造時の準備工程を施す必要が
なく、量産性、経済性の面から有利である。(3) Production method Since multi-layer slabs are manufactured by continuous casting and the slabs are hot rolled, there is no difference in process from the conventional manufacturing method of large steel plates, and the preparation process when manufacturing clad steel plates is simplified. It is advantageous in terms of mass production and economy as there is no need to apply the same.
以下に、熱間圧延以降の製造方法を限定する理由を述べ
る。The reason for limiting the manufacturing method after hot rolling will be described below.
まず、加熱温度については、母材の靭性を確保する点か
ら初期オーステナイト粒は細かい方か良く、このため複
層鋳片の加熱温度は、低い方が望ましい。加熱温度が1
300℃を超えると、オーステナイト粒が粗大化して靭
性を劣化させるので、加熱温度の上限を1300℃とし
た。一方、その下限は高合金鋼の溶体化の観点から、1
100℃以上にすることが必要である。First, regarding the heating temperature, from the point of view of ensuring the toughness of the base material, it is better if the initial austenite grains are finer. Therefore, it is desirable that the heating temperature of the multilayer slab be lower. Heating temperature is 1
If the temperature exceeds 300°C, the austenite grains become coarse and the toughness deteriorates, so the upper limit of the heating temperature was set at 1300°C. On the other hand, from the viewpoint of solution treatment of high alloy steel, the lower limit is 1
It is necessary to raise the temperature to 100°C or higher.
仕上温度が650℃未満になると、高合金鋼の合板の組
織のフェライトが加工を受け、靭性が劣化するので、圧
延工程の仕上温度の下限は650℃とした。また、圧延
終了後の冷却に関しては、空冷あるいは水冷(加速冷却
)のいずれのプロセスを適用してもよい。If the finishing temperature was less than 650°C, the ferrite in the structure of the high-alloy steel plywood would be processed and the toughness would deteriorate, so the lower limit of the finishing temperature in the rolling process was set at 650°C. Furthermore, for cooling after rolling, either air cooling or water cooling (accelerated cooling) may be applied.
なお、本発明は種々の鋼板に適用が可能であるか、主と
して厚鋼板、熱延鋼板並びにこれらを冷間あるいは熱間
加工して製造する鋼管に適用されることが望ましい。The present invention can be applied to various steel plates, and is preferably applied mainly to thick steel plates, hot-rolled steel plates, and steel pipes produced by cold or hot working these.
(実 施 例)
表1に示される化学成分から成る連続鋳造により製造さ
れた複層鋳片を、表2に示されるような圧延条件に従っ
て熱間圧延した。(Example) A multilayer slab manufactured by continuous casting having the chemical components shown in Table 1 was hot rolled according to the rolling conditions shown in Table 2.
このようにして製造した複合鋼板A−Jの母材部分から
試験片を切り取り、引張試験およびシャルピー試験を行
った。A test piece was cut from the base metal portion of the composite steel plate A-J manufactured in this way, and a tensile test and a Charpy test were conducted.
また、これらの複合鋼板を用いて、孔食試験ならびに側
曲げ試験を行った。Furthermore, pitting corrosion tests and side bending tests were conducted using these composite steel plates.
これらの結果を、表2に合わせて示す。These results are also shown in Table 2.
その結果、比較例Iに関しては、内層部のC量が0.0
98%と表層部のC量より高いため、密着性が劣化した
ものである。また、比較例Jに関しては、溶体化処理が
不十分であるため耐孔食性が劣化し、仕上温度が低いた
め靭性も悪くなった。これらに対して、本発明法では孔
食は発生せず、密着性も良好であり、適正な強度、靭性
が得られた。As a result, for Comparative Example I, the amount of C in the inner layer was 0.0
Since the C content was 98%, which was higher than the C content in the surface layer, the adhesion was deteriorated. Furthermore, regarding Comparative Example J, the pitting corrosion resistance deteriorated due to insufficient solution treatment, and the toughness also deteriorated due to the low finishing temperature. In contrast, with the method of the present invention, pitting corrosion did not occur, adhesion was good, and appropriate strength and toughness were obtained.
以上説明したように、この発明によれば、耐食性に優れ
た合わせ材部を有する。複層鋳片を熱間圧延により耐食
性に優れた複合鋼板を製造できる。As explained above, according to the present invention, the laminated material portion has excellent corrosion resistance. Composite steel plates with excellent corrosion resistance can be manufactured by hot rolling multilayer slabs.
(発明の効果)
本発明の耐食性に優れた複合鋼板の製造方法によれば、
鋼板の密着性、耐食性を兼ね備えた複合鋼板を容易にか
つ安価に製造することができる。(Effect of the invention) According to the method of manufacturing a composite steel plate with excellent corrosion resistance of the present invention,
A composite steel plate that has both the adhesion and corrosion resistance of a steel plate can be easily and inexpensively manufactured.
代 理 人teenager Reason Man
Claims (1)
5%Al:0.06%以下Ti:0.005〜0.03
%N:0.005%以下 残部が鉄および不可避不純物からなる複層鋳片を連続鋳
造で製造し、該鋳片を1100〜1300℃に加熱し、
次いで熱間圧延を仕上温度650℃以上で行った後、空
冷または水冷することを特徴とする耐食性に優れた複合
鋼板の製造方法。 2、内部が重量%で Ca:0.001〜0.006%Cu:0.05〜0.
5%Ni:0.05〜0.5%V:0.01〜0.10
%Mo:0.05〜0.30% の1種または2種以上を更に含有し、残部が鉄および不
可避不純物からなる複層鋳片である請求項1記載の耐食
性に優れた複合鋼板の製造方法。[Claims] 1. The surface layer is made of high-alloy steel, and the inside is made of C: 0.06% or less, Si: 0.80% or less, Mn: 0.80-1.50%, Nb: 0.005-0.005% or less. 0.0
5% Al: 0.06% or less Ti: 0.005 to 0.03
%N: 0.005% or less A multilayer slab with the balance consisting of iron and unavoidable impurities is manufactured by continuous casting, and the slab is heated to 1100 to 1300 ° C.
A method for producing a composite steel sheet with excellent corrosion resistance, which comprises hot rolling at a finishing temperature of 650° C. or higher, followed by air cooling or water cooling. 2. Inside is Ca: 0.001-0.006% Cu: 0.05-0.
5%Ni: 0.05-0.5%V: 0.01-0.10
%Mo: 0.05 to 0.30%, and the remaining part is iron and inevitable impurities. Method.
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP2207590A JPH03229819A (en) | 1990-02-02 | 1990-02-02 | Production of clad steel plate excellent in corrosion resistance |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP2207590A JPH03229819A (en) | 1990-02-02 | 1990-02-02 | Production of clad steel plate excellent in corrosion resistance |
Publications (1)
Publication Number | Publication Date |
---|---|
JPH03229819A true JPH03229819A (en) | 1991-10-11 |
Family
ID=12072772
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
JP2207590A Pending JPH03229819A (en) | 1990-02-02 | 1990-02-02 | Production of clad steel plate excellent in corrosion resistance |
Country Status (1)
Country | Link |
---|---|
JP (1) | JPH03229819A (en) |
Cited By (6)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH06256844A (en) * | 1993-03-08 | 1994-09-13 | Nippon Steel Corp | Production of composite steel sheet having excellent corrosion resistance and low-temperature toughness |
WO2013114851A1 (en) * | 2012-01-30 | 2013-08-08 | Jfeスチール株式会社 | Base metal for high-toughness clad steel plate giving weld with excellent toughness, and process for producing said clad steel plate |
WO2013175793A1 (en) * | 2012-05-23 | 2013-11-28 | Jfeスチール株式会社 | Base material for high-toughness clad steel plate having excellent toughness in welded joints, and method for producing said clad steel plate |
CN103507325A (en) * | 2012-06-28 | 2014-01-15 | 浙江兆隆合金股份有限公司 | Non-magnetic high-elasticity copper-steel composite plate and production method thereof |
WO2015059909A1 (en) * | 2013-10-21 | 2015-04-30 | Jfeスチール株式会社 | Austenitic stainless steel clad steel plate and process for manufacturing same |
CN109695000A (en) * | 2017-10-20 | 2019-04-30 | 鞍钢股份有限公司 | Using IF steel as the two-sided titanium steel composite board of transition zone and its high temperature preparation method |
Citations (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS6043465A (en) * | 1983-08-19 | 1985-03-08 | Nippon Kokan Kk <Nkk> | Hot-rolled clad steel plate with superior toughness at low temperature and its manufacture |
JPS63108947A (en) * | 1986-10-24 | 1988-05-13 | Nippon Steel Corp | Continuous casting method for complex steel |
-
1990
- 1990-02-02 JP JP2207590A patent/JPH03229819A/en active Pending
Patent Citations (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS6043465A (en) * | 1983-08-19 | 1985-03-08 | Nippon Kokan Kk <Nkk> | Hot-rolled clad steel plate with superior toughness at low temperature and its manufacture |
JPS63108947A (en) * | 1986-10-24 | 1988-05-13 | Nippon Steel Corp | Continuous casting method for complex steel |
Cited By (9)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH06256844A (en) * | 1993-03-08 | 1994-09-13 | Nippon Steel Corp | Production of composite steel sheet having excellent corrosion resistance and low-temperature toughness |
WO2013114851A1 (en) * | 2012-01-30 | 2013-08-08 | Jfeスチール株式会社 | Base metal for high-toughness clad steel plate giving weld with excellent toughness, and process for producing said clad steel plate |
JP2013177674A (en) * | 2012-01-30 | 2013-09-09 | Jfe Steel Corp | Base material for high-toughness clad steel plate excellent in toughness in welded part, and method for producing the clad steel plate |
WO2013175793A1 (en) * | 2012-05-23 | 2013-11-28 | Jfeスチール株式会社 | Base material for high-toughness clad steel plate having excellent toughness in welded joints, and method for producing said clad steel plate |
CN104321455A (en) * | 2012-05-23 | 2015-01-28 | 杰富意钢铁株式会社 | Base material for high-toughness clad steel plate having excellent toughness in welded joints, and method for producing said clad steel plate |
CN103507325A (en) * | 2012-06-28 | 2014-01-15 | 浙江兆隆合金股份有限公司 | Non-magnetic high-elasticity copper-steel composite plate and production method thereof |
WO2015059909A1 (en) * | 2013-10-21 | 2015-04-30 | Jfeスチール株式会社 | Austenitic stainless steel clad steel plate and process for manufacturing same |
JPWO2015059909A1 (en) * | 2013-10-21 | 2017-03-09 | Jfeスチール株式会社 | Austenitic stainless clad steel sheet and method for producing the same |
CN109695000A (en) * | 2017-10-20 | 2019-04-30 | 鞍钢股份有限公司 | Using IF steel as the two-sided titanium steel composite board of transition zone and its high temperature preparation method |
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