JPH01132716A - Production of martensitic stainless clad steel plate having excellent corrosion resistance, wear resistance and toughness - Google Patents
Production of martensitic stainless clad steel plate having excellent corrosion resistance, wear resistance and toughnessInfo
- Publication number
- JPH01132716A JPH01132716A JP28856587A JP28856587A JPH01132716A JP H01132716 A JPH01132716 A JP H01132716A JP 28856587 A JP28856587 A JP 28856587A JP 28856587 A JP28856587 A JP 28856587A JP H01132716 A JPH01132716 A JP H01132716A
- Authority
- JP
- Japan
- Prior art keywords
- toughness
- corrosion resistance
- steel
- wear resistance
- martensitic stainless
- 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
- 230000007797 corrosion Effects 0.000 title claims abstract description 21
- 238000005260 corrosion Methods 0.000 title claims abstract description 21
- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 17
- 239000010959 steel Substances 0.000 title claims abstract description 17
- 238000004519 manufacturing process Methods 0.000 title claims description 10
- 229910000734 martensite Inorganic materials 0.000 title claims description 6
- 238000001816 cooling Methods 0.000 claims abstract description 14
- 238000005096 rolling process Methods 0.000 claims abstract description 12
- 238000010438 heat treatment Methods 0.000 claims abstract description 9
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 7
- 229910001105 martensitic stainless steel Inorganic materials 0.000 claims abstract description 6
- 229910000975 Carbon steel Inorganic materials 0.000 claims abstract description 5
- 239000010962 carbon steel Substances 0.000 claims abstract description 5
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 5
- 229910052759 nickel Inorganic materials 0.000 claims abstract description 3
- 239000000463 material Substances 0.000 claims description 26
- 239000002131 composite material Substances 0.000 claims description 8
- 229910001566 austenite Inorganic materials 0.000 abstract description 6
- 239000010953 base metal Substances 0.000 abstract description 6
- 238000005253 cladding Methods 0.000 abstract description 5
- 238000005098 hot rolling Methods 0.000 abstract description 5
- 229910052799 carbon Inorganic materials 0.000 abstract description 4
- 229910001220 stainless steel Inorganic materials 0.000 abstract description 3
- 239000010935 stainless steel Substances 0.000 abstract description 2
- 239000002184 metal Substances 0.000 abstract 3
- 229910052751 metal Inorganic materials 0.000 abstract 3
- 229910045601 alloy Inorganic materials 0.000 abstract 1
- 239000000956 alloy Substances 0.000 abstract 1
- 239000002648 laminated material Substances 0.000 description 12
- 238000000034 method Methods 0.000 description 8
- 230000007423 decrease Effects 0.000 description 6
- 239000000047 product Substances 0.000 description 5
- 229910000963 austenitic stainless steel Inorganic materials 0.000 description 4
- 239000000969 carrier Substances 0.000 description 4
- 238000005336 cracking Methods 0.000 description 4
- 230000000694 effects Effects 0.000 description 4
- 229910052758 niobium Inorganic materials 0.000 description 4
- 239000002244 precipitate Substances 0.000 description 4
- 229910052720 vanadium Inorganic materials 0.000 description 4
- 238000001363 water suppression through gradient tailored excitation Methods 0.000 description 4
- 229910000859 α-Fe Inorganic materials 0.000 description 4
- MUBZPKHOEPUJKR-UHFFFAOYSA-N Oxalic acid Chemical compound OC(=O)C(O)=O MUBZPKHOEPUJKR-UHFFFAOYSA-N 0.000 description 3
- 229910052698 phosphorus Inorganic materials 0.000 description 3
- 239000002002 slurry Substances 0.000 description 3
- 229910001563 bainite Inorganic materials 0.000 description 2
- 229910052750 molybdenum Inorganic materials 0.000 description 2
- 230000001376 precipitating effect Effects 0.000 description 2
- 230000000717 retained effect Effects 0.000 description 2
- VEXZGXHMUGYJMC-UHFFFAOYSA-M Chloride anion Chemical compound [Cl-] VEXZGXHMUGYJMC-UHFFFAOYSA-M 0.000 description 1
- 238000005275 alloying Methods 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- 230000000052 comparative effect Effects 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- 238000000866 electrolytic etching Methods 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 238000004880 explosion Methods 0.000 description 1
- 230000004927 fusion Effects 0.000 description 1
- 238000005304 joining Methods 0.000 description 1
- 239000000203 mixture Substances 0.000 description 1
- 238000005121 nitriding Methods 0.000 description 1
- 229910052757 nitrogen Inorganic materials 0.000 description 1
- 235000006408 oxalic acid Nutrition 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 238000005496 tempering Methods 0.000 description 1
- RMLPZKRPSQVRAB-UHFFFAOYSA-N tris(3-methylphenyl) phosphate Chemical compound CC1=CC=CC(OP(=O)(OC=2C=C(C)C=CC=2)OC=2C=C(C)C=CC=2)=C1 RMLPZKRPSQVRAB-UHFFFAOYSA-N 0.000 description 1
- 238000003466 welding 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
Landscapes
- 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 Steel (AREA)
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、耐摩耗性および靭性に優れたマルテン
サイトステンレスクラツド鋼の製造方法に関し、特にス
ラリー輸送管等のプロダクトキャリアや水門などに適し
たマルテンサイトステンレスクラツド鋼の製造方法に関
する。[Detailed Description of the Invention] <Industrial Application Field> The present invention relates to a method for manufacturing martensitic stainless clad steel having excellent corrosion resistance, wear resistance and toughness, and is particularly applicable to product carriers such as slurry transport pipes, water gates, etc. The present invention relates to a method for producing a suitable martensitic stainless clad steel.
〈従来の技術〉
従来、耐食性および耐摩耗性が要求されるプロダクトキ
ャリアや水門などにはビッカース硬さが２００以上の高
強度オーステナイトステンレス鋼５ＵＳ３０４Ｎ２が用
いられている。<Prior Art> Conventionally, high-strength austenitic stainless steel 5US304N2 with a Vickers hardness of 200 or more has been used for product carriers, water gates, etc. that require corrosion resistance and wear resistance.
オーステナイトステンレス鋼の耐摩耗性については高強
度化した方が有利であり、たとえばビッカース硬さで３
００以上あれば使用寿命が格段に延びることが知られて
いる。それには高強度化に効果のあるＮ、 Ｍｏ、
Ｖ、 Ｎｂ等の添加が有効であるが、これら元素の多量
の添加は、熱間加工性を低下させるため、添加量には限
界があり、ビッカース硬さを３００以上にすることは難
しい、また、オーステナイトステンレス鋼を低温で圧延
することにより格子欠陥を導入して高強度化する技術が
開発されているが、このいわゆるＴＭＣＰ（Ｔｈｅｒｍ
ａｌ Ｍｅｃｈａｎ−ｉｃａ！ Ｃｏｎｔｒｏｌ Ｐｒ
ｏｃｅｓｓ） による高強度化では残留応力が大きく
なってオーステナイトステンレス鋼の場合応力腐食割れ
を生じるのでビッカース硬さを３００以上にすることは
現実的ではない。Regarding the wear resistance of austenitic stainless steel, it is advantageous to increase its strength, for example, the Vickers hardness is 3.
It is known that if the value is 00 or more, the service life will be significantly extended. For this purpose, N, Mo, which is effective in increasing strength, are used.
Addition of V, Nb, etc. is effective, but addition of large amounts of these elements reduces hot workability, so there is a limit to the amount of addition, and it is difficult to increase the Vickers hardness to 300 or more. , a technology has been developed to increase the strength of austenitic stainless steel by introducing lattice defects by rolling it at low temperatures.
al Mechan-ica! Control Pr
Increasing the strength by increasing the strength by increasing the strength of the steel increases the residual stress and causes stress corrosion cracking in the case of austenitic stainless steel, so it is not realistic to increase the Vickers hardness to 300 or more.
オーステナイトステンレス鋼に比べて一般に、溶接性、
靭性、延性の点で若干劣るが、強度の点では優れている
綱としてマルテンサイトステンレス鋼がある。特にＮｉ
を添加して溶接性、靭性を向上させたＮｉ添加マルテン
サイトステンレス鋼は焼ならし焼もどしを処理すること
によりＨ，−２７０゜ｖＥｏ ”１５ｋｇｆ・−の特性
を示すが、これは硬度の点でまだ不満足である。またこ
の鋼は熱延のままではｎ、は３５０であるが、ＶＦ、０
は５．２ｋｇＦ ・−と低く靭性の点で使用することが
できない。Generally better weldability compared to austenitic stainless steels.
Martensitic stainless steel is a steel that is slightly inferior in toughness and ductility, but superior in strength. Especially Ni
Ni-added martensitic stainless steel, which has improved weldability and toughness by adding Ni, shows characteristics of H, -270°vEo "15kgf・- by normalizing and tempering, but this is due to the hardness point This is still unsatisfactory.In addition, when this steel is hot-rolled, n is 350, but VF, 0
It cannot be used because of its low toughness of 5.2 kgF.
また、ステンレス鋼の表面を硬化させる方法として窒化
処理があるが、この方法では構造物が大型になった場合
、十分に対処できないことと、表面のごく限られた層し
か経済的に窒化できないことが欠点である。In addition, nitriding is a method of hardening the surface of stainless steel, but this method cannot adequately handle large structures, and only a limited layer of the surface can be nitrided economically. is a drawback.
〈発明が解決しようとする問題点〉
本発明は耐食性に優れ、靭性がＶＥＯで２０ｋｇＦ・−
以上を保持した状態で表面硬さＨｖが３００以上の、ス
ラリー輸送管等のプロダクトキャリアや水門用の材料と
して非常に好適な素材の製造方法を提供するものである
。<Problems to be solved by the invention> The present invention has excellent corrosion resistance and has a toughness of 20 kgF・- in VEO.
The present invention provides a method for producing a material which has a surface hardness Hv of 300 or more while maintaining the above properties and is very suitable as a material for product carriers such as slurry transport pipes and water gates.
く問題解決のための手段〉
本発明は、ｃ 二ｏ、ｏｓ％以下、Ｃｒ：１１〜１５％
およびＮｉ：３〜６％を含有するマルテンサイトステン
レス鋼を合せ材とし、Ｃ： ０．０１〜０．２０％、Ｓ
ｉ：０．０１〜１．０％およびＭｎ ： ０．５（１〜
２．０％を含有する炭素鋼を母材とする複合スラブを１
０００℃以上で加熱したのち、９００〜７５０℃の温度
範囲で圧下率１０％以上の圧延を行い、７５０℃以上か
ら２℃／Ｓ以上の冷却速度で１５０℃以下まで冷却する
ことを特徴とする耐食性、耐摩耗性および靭性に優れた
マルテンサイトステンレスクラツド鋼の製造方法である
。Means for Solving Problems〉 The present invention is characterized in that c2o, os% or less, Cr: 11 to 15%
and martensitic stainless steel containing Ni: 3 to 6%, C: 0.01 to 0.20%, S
i: 0.01~1.0% and Mn: 0.5 (1~
A composite slab whose base material is carbon steel containing 2.0%
After heating at 000°C or more, rolling is performed at a reduction rate of 10% or more in a temperature range of 900 to 750°C, and cooling from 750°C or more to 150°C or less at a cooling rate of 2°C/S or more. This is a method for producing martensitic stainless clad steel that has excellent corrosion resistance, wear resistance, and toughness.
く作 用〉
本発明者らは複合鋼板の機械的性質は混合剤を示すこと
が多いことに着目し、合わせ材の靭性が多少低（でも、
高靭性の材料と複合化することにより、前述した従来の
問題点を解決したものである。Effect> The present inventors focused on the fact that the mechanical properties of composite steel sheets often show the admixture, and found that the toughness of the composite material was somewhat low (but
By combining it with a highly tough material, the above-mentioned conventional problems have been solved.
即ち、複合鋼板化するに際して、合わせ材及び母材に夫
々の機能を賦与するために必要なＴＭＣＰ条件を、合わ
せ材、母材の成分とともに種々検討した結果、合わせ材
にＮｉ添加のマルテンサイトステンレス鋼、母材にＣ，
Ｓｉ、 Ｍｎ量を特定範囲に制限した炭素鋼を用いて、
特定条件の熱間圧延を行なえば、合わせ材の耐食性を損
うことなく、高強度化することができ、なおかつ母材の
靭性も確保できることを見い出した。In other words, as a result of various studies on the TMCP conditions necessary to impart the respective functions to the laminated material and the base material, together with the components of the laminated material and the base material, when creating composite steel sheets, we found that martensitic stainless steel with Ni added to the laminated material. Steel, C in the base material,
Using carbon steel with Si and Mn content limited to a specific range,
It has been discovered that by hot rolling under specific conditions, it is possible to increase the strength of the laminated material without impairing its corrosion resistance, and it is also possible to ensure the toughness of the base material.
本発明の成分および製造方法の限定理由を以下に述べる
。The reasons for limiting the components and manufacturing method of the present invention will be described below.
（１） 合わせ材
Ｃを０．０５％以下にするのは７５０℃〜９００℃にお
ける熱間圧延中あるいは冷却途中にＣｒ炭化物が析出し
て、耐食性が低下するのを防ぐためである。(1) The reason why the content of the laminated material C is 0.05% or less is to prevent Cr carbide from precipitating during hot rolling at 750° C. to 900° C. or during cooling, thereby preventing a decrease in corrosion resistance.
Ｃ「を１１−１５％に限定するのは１１％より少ないと
耐食性が低下するためであり、一方１５％より多いとｎ
ｔ点が低くなりすぎて残留オーステナイトの生成が多く
なり十分な耐摩耗性を発渾できなくなるためである。The reason why C' is limited to 11-15% is that less than 11% lowers the corrosion resistance, whereas more than 15%
This is because if the t point becomes too low, a large amount of retained austenite is generated, making it impossible to develop sufficient wear resistance.
Ｎｉは加熱時にオーステナイト単相にするために必要で
あり、また耐食性も向上させる。 Ｎｉを３〜６％に限
定したのは３％よりも少ないと７５０〜９００℃の圧延
途中で第２相が析出し耐食性の低下、強度の低下を招く
ためである。一方、６％より多いとＭ１点が低下して圧
延後の冷却によっても一部のオーステナイトがマルテン
サイトに変態せずに残留オーステナイトとして残り、耐
摩耗性を低下させるためである。Ni is necessary to make the austenite single phase during heating, and also improves corrosion resistance. The reason why Ni is limited to 3 to 6% is because if it is less than 3%, a second phase will precipitate during rolling at 750 to 900°C, resulting in a decrease in corrosion resistance and strength. On the other hand, if it exceeds 6%, the M1 point decreases, and even after cooling after rolling, some austenite remains as retained austenite without being transformed into martensite, resulting in a decrease in wear resistance.
その他合せ材の硬度をさらに上げるために、Ｍｏ。In order to further increase the hardness of the other laminates, Mo.
Ｎｂ、 Ｖ等を１．０％以下添加できる。Nb, V, etc. can be added in an amount of 1.0% or less.
（２） 母材
Ｃを０．０１〜０．２０％に限定したのはＣが０．０１
％より少ないと７５０〜９００℃の圧延途中で生成する
フェライト量が多くなりすぎて、強度不足を生じるため
である。０．２％より多いと、十分な靭性が確保できな
くなるためである。(2) The base material C is limited to 0.01 to 0.20% because C is 0.01%.
%, the amount of ferrite generated during rolling at 750 to 900° C. becomes too large, resulting in insufficient strength. This is because if the amount exceeds 0.2%, sufficient toughness cannot be ensured.
Ｓｉは１．０％より多く含有すると靭性が低下するため
、１．０％以下に限定した。また、製鋼時の脱酸を有効
ならしめるためにはＳｉは０．０１％以上必要である。If Si is contained more than 1.0%, the toughness decreases, so it is limited to 1.0% or less. Further, in order to make deoxidation effective during steel manufacturing, Si is required to be present in an amount of 0.01% or more.
Ｍｎを０．５０〜２．０％に限定したのは０．５％より
少ないとベイナイト組織が得られず強度不足を生じるた
めである。一方２．０％より多いと圧延後の冷却でアル
テンサイドが生成し、靭性が低下するためである。The reason why Mn is limited to 0.50 to 2.0% is because if it is less than 0.5%, a bainite structure cannot be obtained, resulting in insufficient strength. On the other hand, if it exceeds 2.0%, altenside will be generated during cooling after rolling, resulting in a decrease in toughness.
その他母材の強度を上げるためにＮｂ、 Ｖ、 Ｍｏ
。In order to increase the strength of other base materials, Nb, V, Mo
.
等をＮｂ ： ０．００５〜０．２０％、 Ｖ ：
０．００５〜０．２０％。etc. Nb: 0.005-0.20%, V:
0.005-0.20%.
Ｍｏ ： ０．０１〜０．５０％程度添加してもよい。Mo: May be added in an amount of about 0.01 to 0.50%.
（３）熱間圧延
加熱温度を１０００℃以上に限定したのは合わせ材およ
び母材を夫々オーステナイト単相域まで加熱することに
より合金元素の再固溶を促進するためである。なお、続
いて実施する圧延工程で合わせ材と母材を接合させる場
合には合わせ材および母材に第２相が析出しない温度ま
で加熱温度を上げることが接合強度向上に必要であり、
１２５０〜１３００“Ｃに加熱することが効果的である
。(3) The reason why the hot rolling heating temperature is limited to 1000° C. or higher is to promote re-solid solution of the alloying elements by heating the composite material and the base material to the austenite single phase region, respectively. In addition, when joining the laminated material and the base material in the subsequent rolling process, it is necessary to increase the heating temperature to a temperature at which the second phase does not precipitate in the laminated material and the base material in order to improve the joint strength.
Heating to 1250-1300"C is effective.
次に７５０〜９００℃において少なくとも１０％以上の
圧延を行なう理由は母材の＆ｌ１ｍ中にフェライトを析
出させるためには７５０〜９００’Ｃで圧延することが
必要であり、フェライトを細かく析出させるためには７
５０〜９００℃ｒ１Ｏ％以上の圧延を行うことが必要で
ある。Next, the reason for rolling at least 10% at 750-900°C is that in order to precipitate ferrite in the &l1m of the base metal, it is necessary to roll at 750-900'C, and in order to finely precipitate ferrite. to 7
It is necessary to perform rolling at 50-900°C r1O% or more.
また、７５０℃からの冷却速度を２℃／Ｓ以上に限定し
たのは、これよりも冷却速度が遅いとフェライトが多（
なり、あるいは上部ベイナイトが析出して母材の靭性を
低下させるためである。Also, the reason why we limited the cooling rate from 750°C to 2°C/S or more is because if the cooling rate is slower than this, there will be a lot of ferrite (
This is because upper bainite precipitates and reduces the toughness of the base metal.
冷却停止温度を１５０’Ｃ以下に限定したのは合わせ材
に第２相が析出して耐食性が低下するのを防ぐためであ
る。The reason why the cooling stop temperature was limited to 150'C or less was to prevent the second phase from precipitating in the laminated material and reducing the corrosion resistance.
なお、本発明に関する合わせ材および母材は熱間圧延前
に既にクラッドとして接合されていてもあるいは単なる
組立て状態であってもその効果は変わらない、もちろん
、クラッドの製造法は溶接組立法、鋳包み法、爆着法、
溶融接合法などのいずれであってもよい。Furthermore, even if the laminated material and the base material related to the present invention are already joined as a cladding before hot rolling or are simply assembled, the effect remains the same.Of course, the cladding can be manufactured by welding assembly method, casting method, etc. Wrapping method, explosion method,
Any method such as fusion bonding may be used.
〈実施例〉
板厚３０ｆｆｌＩｌの比較例としてのｃ：ｏ、ｒｏ％、
Ｓｉ：０．２０％、Ｍｎ ：０．７ ％、 Ｐ
： ０．０１５ ％、 Ｓ ： ０．００５％
、 Ｃｒ ： １３．５％、の５ＵＳ４１０． Ｃ：
０．０６％、Ｎｉニア、８％、Ｃｒ ： １８．１％、
Ｎ１．２０％、Ｎｂ ： ０．０８％、 Ｐ ：０．０
２５ ％、 Ｓ ：０．００３ ％、 Ｓｉ
： ０．５０％、 Ｍｎ ： １．５０％の５ＵＳ
３０４ならびにＣ：０．０４％、 Ｃｒ ： １２．８
％＋Ｎｉ：３．５ ％、Ｓｉ：０．５ ％、 Ｍｎ
： ０．８９％、 Ｐ ：０．０２５％、 Ｓ
：０．００３％の１３Ｃｒ ５ Ｎｉを合わせ材に
、板厚１００ｍ５のＣ： ０．０４％、 Ｓｉ ： ０
．２５％、Ｍｒ＋：１．２％。<Example> c: o, ro%, as a comparative example of plate thickness 30fflIl,
Si: 0.20%, Mn: 0.7%, P
: 0.015%, S: 0.005%
, Cr: 13.5%, 5US410. C:
0.06%, Ni near, 8%, Cr: 18.1%,
N1.20%, Nb: 0.08%, P: 0.0
25%, S: 0.003%, Si
: 0.50%, Mn: 1.50% 5US
304 and C: 0.04%, Cr: 12.8
%+Ni: 3.5%, Si: 0.5%, Mn
: 0.89%, P: 0.025%, S
:0.003% 13Cr5Ni as laminated material, plate thickness 100m5 C: 0.04%, Si: 0
．． 25%, Mr+: 1.2%.
Ｐ ： ０．０１５％、 Ｓ ： ０．００３％の鋼
を母材として用い、まず合わせ材を母材に重ね合わせた
のち第１図に示すように周囲を溶接して組立てスラブに
した。Using steel with P: 0.015% and S: 0.003% as a base material, the laminated material was first superimposed on the base material, and then the periphery was welded as shown in FIG. 1 to make an assembled slab.
このスラブを１２５０’Ｃで加熱したのち、表１に示す
圧延スケジュール、冷却条件で板厚３０ｍに仕上げた。After heating this slab at 1250'C, it was finished to a thickness of 30 m using the rolling schedule and cooling conditions shown in Table 1.
これらクラツド鋼板の表面ビッカース硬さ、耐食性、母
材靭性を調べた結果を表２に示す、 １３Ｃｒ５Ｎｉ鋼
に比ヘテ５Ｕｓ４１０．５ＵＳ３０４の合わせ材は耐食
性および表面硬さの点で劣る口上がわかる。ま表
２
傘粒界腐食惑受性 −−○ 良好 Δ やや劣る ×
劣る１０％しゅう酸電解エッチによる試験
傘傘応力腐食割れ性 Ｏ割れなし、 × 割れあ
り４２％２％塩化マグネシラによる試験 ｂ、Ｉｌ、
Ｘ４８ｈた、本発明以外の製造方法では母材の良好な靭
性が得られないことがわかる。The results of investigating the surface Vickers hardness, corrosion resistance, and base metal toughness of these clad steel plates are shown in Table 2. It can be seen that the composite material of 13Cr5Ni steel and 5Us410.5US304 is inferior in terms of corrosion resistance and surface hardness. Ma table
2 Umbrella intergranular corrosion acceptability −−○ Good Δ Slightly poor ×
Inferior test with 10% oxalic acid electrolytic etching Umbrella stress corrosion cracking resistance No cracking, × with cracking 42% Test with 2% magnesila chloride b, Il,
It can be seen that good toughness of the base material cannot be obtained by manufacturing methods other than the present invention.
即ち本発明では合せ材および母材の組成と製造方法とが
一体となって、耐食性、耐摩耗性および靭性に優れた製
品が得られるのである。That is, in the present invention, the compositions of the laminate and base material and the manufacturing method are integrated to provide a product with excellent corrosion resistance, wear resistance, and toughness.
〈発明の効果〉
本発明により製造したステンレスクラツド鋼板は、合わ
せ材が硬く、母材の靭性が優れているため、従来の単一
材では得ることが困難であった耐摩耗性と靭性、耐食性
を兼ね備えた材料を安価に得ることを可能にした。この
材料は腐食性スラリー輸送用構造材料としてのプロダク
トキャリアあるいは水門材等に用いて、従来材に比べて
格段の長寿命を有し、その経済的効果は大きい。<Effects of the Invention> The stainless clad steel sheet manufactured according to the present invention has a hard laminated material and excellent toughness of the base material, so it has high wear resistance and toughness that were difficult to obtain with conventional single materials. This makes it possible to obtain materials with corrosion resistance at low cost. This material is used as a structural material for transporting corrosive slurry, such as product carriers or water gate materials, and has a much longer lifespan than conventional materials, and has great economic effects.
第１図はスラブの組立状況を示す図である。 FIG. 1 is a diagram showing how the slabs are assembled.
Claims (1)
３〜６％を含有するマルテンサイトステンレス鋼を合せ
材とし、Ｃ：０．０１〜０．２０％、Ｓｉ：０．０１〜
１．０％およびＭｎ：０．５０〜２．０％を含有する炭
素鋼を母材とする複合スラブを１０００℃以上で加熱し
たのち、９００〜７５０℃の温度範囲で圧下率１０％以
上の圧延を行い、７５０℃以上から２℃／Ｓ以上の冷却
速度で１５０℃以下まで冷却することを特徴とする耐食
性、耐摩耗性および靭性に優れたマルテンサイトステン
レスクラッド鋼の製造方法。C: 0.05% or less, Cr: 11-15% and Ni:
Martensitic stainless steel containing 3 to 6% is used as a composite material, C: 0.01 to 0.20%, Si: 0.01 to
After heating a composite slab whose base material is carbon steel containing 1.0% and Mn: 0.50 to 2.0% at a temperature of 1000°C or higher, A method for producing martensitic stainless clad steel having excellent corrosion resistance, wear resistance and toughness, which comprises rolling and cooling from 750°C or higher to 150°C or lower at a cooling rate of 2°C/S or higher.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP28856587A JPH01132716A (en) | 1987-11-17 | 1987-11-17 | Production of martensitic stainless clad steel plate having excellent corrosion resistance, wear resistance and toughness |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP28856587A JPH01132716A (en) | 1987-11-17 | 1987-11-17 | Production of martensitic stainless clad steel plate having excellent corrosion resistance, wear resistance and toughness |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH01132716A true JPH01132716A (en) | 1989-05-25 |
Family
ID=17731899
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP28856587A Pending JPH01132716A (en) | 1987-11-17 | 1987-11-17 | Production of martensitic stainless clad steel plate having excellent corrosion resistance, wear resistance and toughness |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH01132716A (en) |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US5213905A (en) * | 1991-03-01 | 1993-05-25 | Creusot-Loire Industrie | Process for producing a composite flat product, stainless armor and armored storage tank obtained by this process |
| JP2006007765A (en) * | 2004-05-28 | 2006-01-12 | Asahi Rubber:Kk | Manufacturing process of lens for semiconductor optical device |
-
1987
- 1987-11-17 JP JP28856587A patent/JPH01132716A/en active Pending
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US5213905A (en) * | 1991-03-01 | 1993-05-25 | Creusot-Loire Industrie | Process for producing a composite flat product, stainless armor and armored storage tank obtained by this process |
| JP2006007765A (en) * | 2004-05-28 | 2006-01-12 | Asahi Rubber:Kk | Manufacturing process of lens for semiconductor optical device |
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