JP3047752B2 - Manufacturing method of titanium clad steel sheet - Google Patents
Manufacturing method of titanium clad steel sheetInfo
- Publication number
- JP3047752B2 JP3047752B2 JP6283629A JP28362994A JP3047752B2 JP 3047752 B2 JP3047752 B2 JP 3047752B2 JP 6283629 A JP6283629 A JP 6283629A JP 28362994 A JP28362994 A JP 28362994A JP 3047752 B2 JP3047752 B2 JP 3047752B2
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- JP
- Japan
- Prior art keywords
- rolling
- titanium
- steel
- reduction
- hot
- 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.)
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- Laminated Bodies (AREA)
- Metal Rolling (AREA)
Description
【０００１】[0001]
【産業上の利用分野】本発明は、チタンクラッド鋼板の
製造方法に関する。The present invention relates to a method of <br/> manufacturing titanium clad steel plate.
【０００２】[0002]
【従来の技術】クラッド材は、それぞれの異種金属を層
状に接合したもので、それぞれの金属が有している優れ
た特性を併せ持つ材料として注目されている。特に、チ
タンクラッド鋼は、鋼の優れた強度、熱伝導性および溶
接性とチタンの高耐食性とを併せ持つ材料として、化学
プラント用および海洋防食用等の高い強度と耐食性が要
求される部材への適用が進められている。2. Description of the Related Art A clad material is formed by joining different kinds of metals in layers, and is attracting attention as a material having excellent characteristics of each metal. In particular, titanium clad steel is a material that combines the excellent strength, thermal conductivity and weldability of steel with the high corrosion resistance of titanium. Application is in progress.
【０００３】現在、チタンクラッド鋼板は大別して爆着
法と圧延法により製造されている。[0003] At present, titanium clad steel sheets are roughly produced by an explosion method and a rolling method.
【０００４】爆着法は爆発のエネルギーを利用してチタ
ンと鋼の接合を行うもので、接合材のサイズ、形状に制
限が大きいことに加え、接合施工を実施する場所につい
ても大きな制約を受けるため、大量生産には不向きであ
り、爆着法で安価なチタンクラッド鋼板を製造すること
は困難である。[0004] The bombardment method uses the energy of the explosion to join titanium and steel, so that the size and shape of the joining material are greatly limited, and the location of the joining work is also greatly restricted. Therefore, it is not suitable for mass production, and it is difficult to produce an inexpensive titanium clad steel sheet by the explosion method.
【０００５】圧延法では、従来の圧延設備を利用するこ
とができる上に、板厚の制限が小さく、生産性も比較的
高いことから、圧延法は爆着法と比べ有利な製造方法で
あるということができる。しかし、熱間圧延による接合
法であるためにチタンと鋼の接合界面に脆弱なＴｉ−Ｆ
ｅ系金属間化合物やＴｉＣ炭化物が形成される可能性が
高く、この金属間化合物や炭化物の形成により、クラッ
ド鋼板の界面強度や耐食性が著しく低下することが懸念
される。[0005] In the rolling method, the conventional rolling equipment can be used, the thickness is limited, and the productivity is relatively high. Therefore, the rolling method is a more advantageous production method than the explosion method. It can be said. However, since the joining method is based on hot rolling, the fragile Ti-F is present at the joining interface between titanium and steel.
There is a high possibility that an e-based intermetallic compound or TiC carbide is formed, and there is a concern that the formation of the intermetallic compound or carbide will significantly reduce the interface strength and corrosion resistance of the clad steel sheet.
【０００６】これまで、このような接合界面でのＴｉ−
Ｆｅ系金属間化合物やＴｉＣ炭化物の形成に対しては、
圧延接合温度および中間材によるＦｅ−Ｔｉの相互拡散
の防止という観点から、種々の取り組みがなされてい
る。Heretofore, Ti-
For the formation of Fe-based intermetallic compounds and TiC carbides,
Various approaches have been taken from the viewpoint of preventing the inter-diffusion of Fe-Ti by the rolling joining temperature and the intermediate material.
【０００７】例えば、チタンと鋼との間に中間材とし
て、炭素量が０．０３％以下の薄鋼板を介在させる方法
（特開昭６２−１５８５８４号公報、特開昭６３−５６
３７０号公報参照）や、０．０１％以下の鋼とニッケル
の薄板（特開昭６２−１９７２８５号公報参照）、０．
０１％以下の炭素鋼の薄板（特開平５−８０５９号公報
参照）、あるいは銅とニッケルの薄板（特開昭６０−１
７０５８６号公報参照）等の２層を介在させる方法が開
示されている。For example, a method of interposing a thin steel sheet having a carbon content of 0.03% or less as an intermediate material between titanium and steel (JP-A-62-158584, JP-A-63-56).
No. 370), a thin plate of steel and nickel of 0.01% or less (see Japanese Patent Application Laid-Open No. 62-197285), 0.
01% or less carbon steel sheet (see JP-A-5-8059) or copper and nickel sheet (see JP-A-60-1).
No. 70586) is disclosed.
【０００８】また、中間材を使わないで、特定の圧延条
件、即ち熱延加熱温度を８００〜８８５℃、圧延終了温
度を７００℃以上とする方法（特開昭５６−１６３００
５号公報参照）や、８５０〜９００℃に加熱し、圧下比
２以上で圧延し、次いで６５０〜９５０℃で熱処理を行
った後、圧下比１．１〜５で熱間圧延を行う方法（特開
昭６０−２１３３７８号公報参照）、あるいは７５０℃
以上の圧延パス間隔を３０ｓ以内とする方法（特開平４
−１２３８８３号公報参照）などが開示されている。[0008] Also, a method in which specific rolling conditions, that is, a hot rolling heating temperature of 800 to 885 ° C and a rolling end temperature of 700 ° C or more, without using an intermediate material (JP-A-56-16300).
No. 5) or a method of rolling at a reduction ratio of 2 or more by heating to 850 to 900 ° C., performing heat treatment at 650 to 950 ° C., and then performing hot rolling at a reduction ratio of 1.1 to 5 ( JP-A-60-213378) or 750 ° C
A method in which the above-mentioned rolling pass interval is set within 30 seconds (Japanese Unexamined Patent Application Publication No.
No. 123883).
【０００９】[0009]
【発明が解決しようとする課題】しかし、上記のような
方法を適用し、既存の鋼用の熱延設備によりチタンクラ
ッド鋼板、特にその薄板を製造する場合には、それぞれ
次の問題がある。However, when the above-described method is applied to manufacture a titanium clad steel sheet, particularly a thin sheet thereof, using existing hot rolling equipment for steel, there are the following problems.
【００１０】例えば、鋼の既存熱延設備では、鋼材スラ
ブを１０００℃以上の高温に加熱し、連続圧延ミルを用
いて総圧下率８０％以上の高い圧下率により、多量の薄
鋼板を低コストで製造することができる。しかし、この
設備と方法をチタンクラッド鋼板の製造に適用した場
合、前記の中間材を用いる方法では、圧延による圧下率
が大きいために、圧延中に中間材と母材（鋼）、合わせ
材（チタン）との変形抵抗の違いから、中間材が切断さ
れ、鋼とチタンが直接接触して界面にＴｉ−Ｆｅ系の金
属間化合物が形成されることとなり、安定した高い接合
強度を得ることが難しい。[0010] For example, in the existing hot rolling equipment for steel, a steel material slab is heated to a high temperature of 1000 ° C or more, and a continuous rolling mill is used to produce a large amount of thin steel sheets at a high reduction rate of 80% or more, so that a large amount of thin steel sheets can be produced at low cost. Can be manufactured. However, when this equipment and method are applied to the production of a titanium clad steel sheet, in the method using the intermediate material, since the rolling reduction by rolling is large, the intermediate material, the base material (steel), and the composite material ( Due to the difference in deformation resistance between the steel and titanium, the intermediate material is cut, and the steel and titanium come into direct contact with each other to form a Ti-Fe-based intermetallic compound at the interface, thereby obtaining stable high bonding strength. difficult.
【００１１】前記特開昭５６−１６３００５号公報に示
される中間材を使わない方法には、その熱延加熱温度条
件が低いことから、１０００℃以上の加熱を必要とする
既存の鋼用熱延設備を適用することができない。前記特
開昭６０−２１３３７８号公報に示されるような熱処理
を中間に用いる方法では、クラッド鋼板のコストが高く
なる。The method using no intermediate material disclosed in the above-mentioned Japanese Patent Application Laid-Open No. 56-163005 discloses an existing hot rolling method for steel which requires heating at 1000 ° C. or more because of its low hot rolling heating temperature condition. Equipment cannot be applied. The method using the intermediate heat treatment as disclosed in JP-A-60-213378 increases the cost of the clad steel sheet.
【００１２】前記特開平４−１２３８８３号公報のよう
に、単に７５０℃以上の圧延のパス間隔だけを定める方
法では、圧下比が小さい場合には新生面による接合面積
が小さいため、高い接合強度が得られない。また、高い
温度（９００℃以上）で圧延を終了した場合には、圧延
時に接合界面に金属間化合物が形成されていない界面で
も圧延終了時の温度が高いため、冷却中に界面に金属間
化合物が生じる。このため、高い接合強度が得られなく
なる。In the method of simply determining the pass interval of the rolling at 750 ° C. or higher as in the above-mentioned Japanese Patent Application Laid-Open No. 4-123883, a high bonding strength is obtained because the bonding area due to the new surface is small when the rolling reduction ratio is small. I can't. Further, when the rolling is completed at a high temperature (900 ° C. or higher), the temperature at the end of rolling is high even at the interface where the intermetallic compound is not formed at the joining interface during rolling. Occurs. Therefore, high bonding strength cannot be obtained.
【００１３】母材炭素鋼の炭素濃度が、例えば０．０３
mass％のように高いと、接合界面にＴｉＣ炭化物が形成
され、高い接合強度を得ることができない。The carbon concentration of the base carbon steel is, for example, 0.03
If it is as high as mass%, TiC carbide is formed at the joint interface, and high joint strength cannot be obtained.
【００１４】本発明は上記の問題点を解決するためにな
されたものであり、本発明の目的は安定した高い接合強
度を有するチタンクラッド鋼板を既存の鋼用の熱延設備
を用いて安価に製造する方法を提供することにある。[0014] The present invention has been made to solve the above problems, the aim is inexpensive by using a hot-rolled facilities for titanium clad steel plates existing steel having a stable high bonding strength of the present invention It is to provide a manufacturing method.
【００１５】[0015]
【課題を解決するための手段】本発明の要旨は、次の
(1) および(2) のチタンクラッド鋼板の製造方法にあ
る。 The gist of the present invention is as follows.
(1) and production method near the titanium clad steel plate (2)
You.
【００１６】(1)母材として鋼材、合わせ材としてチタ
ンまたはチタン合金を用い、母材と合わせ材の接合面を
真空排気した後溶接して組み立てた圧延用組立スラブ
を、熱間圧延により接合するチタンクラッド鋼板の製造
方法であって、圧延用組立スラブに第１熱間圧延工程で
９５０〜１１００℃の温度範囲で圧下率１５％以上の圧
延を１パス以上施し、次いで第２熱間圧延工程で９００
℃〜６００℃の温度範囲で圧下率５％以上の圧延を１パ
ス以上施すことを特徴とするチタンクラッド鋼板の製造
方法（第１の方法）。(1) A steel slab is used as a base material and titanium or a titanium alloy is used as a mating material. A joining surface of the base material and the mating material is evacuated and then joined by hot rolling to form a slab for rolling. to method of manufacturing a titanium clad steel plate, the rolling or reduction ratio of 15% applied 1 or more passes in a temperature range of 950 to 1,100 ° C. in the first hot rolling step for rolling the assembly slab, then the second hot rolling 900 in process
A method for producing a titanium-clad steel sheet (1st method), wherein rolling at a rolling reduction of 5% or more is performed in a temperature range of 1 to 600 ° C. in one or more passes.
【００１７】(2)上記(1) の第１熱間圧延工程後、９０
０℃以下まで放冷し、次いで上記(1)の第２熱間圧延工
程を施すことを特徴とするチタンクラッド鋼板の製造方
法（第２の方法）。(2) After the first hot rolling step (1), 90
A method for producing a titanium-clad steel sheet (second method), which is left to cool to 0 ° C. or lower, and then performs the second hot rolling step (1).
【００１８】[0018]
【００１９】上記の各方法において、母材は炭素量０．
０１mass以下の低炭素鋼とし、さらにこの場合には、第
１熱間圧延工程の圧下率の範囲は１５％以上４０％以
下、次の第２熱間圧延工程の圧下率の範囲は５％以上４
０％以下とするのが望ましい。In each of the above methods , the base material has a carbon content of 0.1.
In this case, the range of the rolling reduction in the first hot rolling step is 15% or more and 40% or less, and the range of the rolling reduction in the next second hot rolling step is 5% or more. 4
It is desirable to set it to 0% or less.
【００２０】同じく、母材鋼の炭素量が上記０．０１ma
ss％を超え０．０５％以下の場合には、第１熱間圧延工
程の圧下率は２０％以上、次の第２熱間圧延工程の圧下
率は１０％以上とするのが望ましい。[0020] Similarly, the carbon content of the base steel is 0.01 ma
When it exceeds ss% and is 0.05% or less, it is desirable that the rolling reduction in the first hot rolling step is 20% or more and the rolling reduction in the next second hot rolling step is 10% or more.
【００２１】母材鋼の炭素量が０．０１mass％を超え
０．０５％以下の場合の圧下率の上限は、圧延ミルのパ
ワーおよび圧延用組立スラブの組立強度（圧延中にこの
スラブの先端部の溶接部が剥離しないこと）によって決
まるため、特に限定されず、連続的な圧下が可能な範囲
であればよい。When the carbon content of the base steel is more than 0.01 mass% and less than 0.05%, the upper limit of the rolling reduction is determined by the power of the rolling mill and the assembling strength of the assembling slab for rolling (the leading end of the slab during rolling). Is not particularly limited, as long as it can be continuously reduced.
【００２２】望ましい圧延パス数の上限は、目標板厚に
よっても変わるが６〜２０パス程度である。The upper limit of the desired number of rolling passes varies depending on the target plate thickness, but is about 6 to 20 passes.
【００２３】「圧下率」は、下記式で定義される数値で
ある。"Rolling rate" is a numerical value defined by the following equation.
【００２４】 圧下率（％）＝[（圧延前の板厚−圧延後の板厚）／圧延前の板厚］×100 本発明者らは前記の問題を解決すべく、チタンクラッド
鋼板の接合界面強度低下の原因となる界面の金属間化合
物および炭化物の形成、成長について種々検討し、母材
鋼の炭素量、圧下率および圧延温度を制御することによ
り、形成された金属間化合物および炭化物を破壊し、そ
の厚さを接合強度に影響を与えない程度に小さくすると
ともに、圧延での塑性変形により新たに形成されたチタ
ンと鋼との新生面により、チタンと鋼との接合をなし、
この新生接合面での金属間化合物および炭化物の成長を
抑制することができれば、高い接合強度を有するチタン
クラッド鋼板が得られるという知見を得て、これに基づ
きさらにチタンクラッド鋼板の圧延条件（圧下率、圧延
温度）および母材鋼の炭素量について検討を行った。こ
の予備試験結果を図１および図２により説明する。Reduction ratio (%) = [(thickness before rolling−thickness after rolling) / thickness before rolling] × 100 In order to solve the above-mentioned problem, the present inventors joined a titanium clad steel sheet. Various investigations were made on the formation and growth of intermetallic compounds and carbides at the interface that caused a decrease in interface strength.
By controlling the carbon content, rolling reduction and rolling temperature of the steel , the formed intermetallic compounds and carbides are destroyed, the thickness is reduced to a level that does not affect the joining strength, and the plastic deformation during rolling By the newly formed surface of titanium and steel newly formed by, the joining of titanium and steel,
It has been found that if the growth of intermetallic compounds and carbides at the newly-bonded surface can be suppressed, a titanium-clad steel sheet having a high bonding strength can be obtained. , Rolling temperature) and the carbon content of the base steel . The results of the preliminary test will be described with reference to FIGS.
【００２５】図１は、接合強度に及ぼす圧延温度と圧下
率との影響を示す図である。FIG. 1 is a diagram showing the effect of the rolling temperature and the rolling reduction on the joining strength.
【００２６】母材（鋼）は厚さ８０mm、炭素量約０．０
３％のものを用い、合わせ材はチタン（厚さ２０mm）と
して、中間材を使用せずに圧延用組立スラブ（以下、圧
延用スラブという）を作製し、圧延条件では、圧延温度
を７００〜１１００℃、１パス当たりの圧下率を５〜３
０％とした。連続圧下可否は、圧延中の剥離、母材
（鋼）と合わせ材（チタン）のずれから判定し、さらに
圧延後のクラッド鋼板をシャー切断し、接合部の開口の
有無により評価した。また、圧延後のクラッド鋼板の中
央部からせん断試験片を採取し、接合強度を評価した。The base material (steel) has a thickness of 80 mm and a carbon content of about 0.0
Using a material of 3%, the assembling material is made of titanium (thickness: 20 mm), and an assembled slab for rolling (hereinafter referred to as “rolling slab”) is produced without using an intermediate material. 1100 ° C, 5-3 reduction per pass
0%. The possibility of continuous rolling was determined based on the peeling during rolling and the displacement between the base material (steel) and the composite material (titanium). Further, a shear test piece was sampled from the center of the clad steel sheet after rolling, and the bonding strength was evaluated.
【００２７】図１に示すように、圧延用スラブが剥離し
たり、ずれたりせずに正常に圧下できるための圧延条件
や、高い接合強度を持ったクラッド鋼板を得るための圧
延条件は、その圧延温度と圧下率により規定される。As shown in FIG. 1, the rolling conditions for normal rolling down without separating or shifting the rolling slab and the rolling conditions for obtaining a clad steel sheet having high bonding strength are as follows. Specified by the rolling temperature and rolling reduction.
【００２８】次に、接合強度に係わる母材鋼の炭素量、
圧延温度および圧下率の影響に関する新知見を、図２に
より説明する。Next, the carbon content of the base steel related to the joining strength,
New findings regarding the effects of the rolling temperature and the rolling reduction will be described with reference to FIG.
【００２９】図２は、母材鋼の炭素量が０．０１mass％
以下の場合の接合強度に及ぼす圧延温度および圧下率の
影響を示す図である。基本的な圧延用スラブの組立条件
は図１の場合と同様である。FIG. 2 shows that the carbon content of the base steel is 0.01 mass%.
It is a figure which shows the influence of the rolling temperature and the rolling reduction on the joining strength in the following cases. Basic assembling conditions of the rolling slab are the same as those in FIG.
【００３０】図２に示すように、母材鋼の炭素濃度を
０．０１mass％以下に限定し、かつ適正な範囲の圧下率
を選択することにより、接合界面に形成されるＴｉＣ炭
化物の成長を抑制することができ、圧延工程において作
り出す新生面の割合、即ち圧下率を小さくしても、十分
に圧延が可能となり、高い接合強度を有するチタンクラ
ッド鋼板を得ることができる。As shown in FIG. 2, by limiting the carbon concentration of the base steel to 0.01 mass% or less and selecting an appropriate rolling reduction, the growth of TiC carbide formed at the joint interface can be reduced. Even if the ratio of the new surface created in the rolling step, that is, the rolling reduction, is reduced, rolling can be sufficiently performed, and a titanium-clad steel sheet having high joining strength can be obtained.
【００３１】接合部でのＦｅ原子、Ｔｉ原子の拡散によ
り、Ｔｉ−Ｆｅ系の金属間化合物が生じ、クラッド界面
の接合強度の低下を招くが、α−Ｔｉ中のＦｅの拡散速
度に対して、β−Ｔｉ中の拡散速度は１０倍近く遅く、
α−Ｔｉ／Ｆｅ界面では、β−Ｔｉ／Ｆｅ界面に対して
金属間化合物の成長が抑えられ、高い接合強度が得られ
る。これを実現するには、チタンがα−Ｔｉの結晶構造
となる温度範囲で最終圧延を行う必要がある。このた
め、第１熱間圧延工程の後、９００℃以下（チタンのα
−β変態温度以下）に放冷し、次いで６００℃以上で第
２熱間圧延を施すのが望ましい。The diffusion of Fe atoms and Ti atoms at the junction generates a Ti—Fe intermetallic compound, which lowers the bonding strength at the cladding interface. , Β-Ti diffusion rate is nearly 10 times slower,
At the α-Ti / Fe interface, the growth of the intermetallic compound is suppressed relative to the β-Ti / Fe interface, and high bonding strength can be obtained. To achieve this, it is necessary to perform final rolling in a temperature range in which titanium has an α-Ti crystal structure. For this reason, after the first hot rolling step, 900 ° C. or less (α of titanium)
(−β transformation temperature or less), and then a second hot rolling at 600 ° C. or more is desirable.
【００３２】[0032]
【作用】まず、本発明方法の対象となる圧延用スラブの
組立方法の例を、図３に基づいて説明する。First, an example of a method of assembling a rolling slab to be subjected to the method of the present invention will be described with reference to FIG.
【００３３】図３は圧延用スラブの組立後の断面を示す
図であり、(a) は非対称型スラブ、(b) は対称型スラブ
の場合である。FIGS. 3A and 3B are views showing the cross section of the rolling slab after assembly, wherein FIG. 3A shows the case of an asymmetric slab and FIG. 3B shows the case of a symmetric slab.
【００３４】図３(a) に示すように、非対称型スラブで
は、母材（鋼）１上の四つの周部にスペーサー（鋼）５
および６、中心部に合わせ材２を配置し、合わせ材２の
表面に剥離剤４を塗布し、スペーサー５、６と剥離剤４
との全表面をダミー材（鋼）３で覆い、その後、真空中
（１０-2Torr以下）で溶接により組立てる。As shown in FIG. 3 (a), in the asymmetric slab, spacers (steel) 5
And 6, placing the bonding material 2 in the center, applying a release agent 4 to the surface of the bonding material 2, and applying spacers 5 and 6 to the release agent 4.
Is covered with a dummy material (steel) 3 and then assembled by welding in a vacuum (10 −2 Torr or less).
【００３５】図３(b) に示すように、対称型スラブの場
合では、剥離剤４の線で母材（鋼）１と合わせ材２とが
対称（図では上下）となり、スペーサー５、６の厚さ内
に２枚の合わせ材２、２と剥離剤４が入るように配置す
る。その後、同様に真空中溶接により組立てる。図示す
るように、この場合はダミー材は用いない。As shown in FIG. 3B, in the case of a symmetrical slab, the base material (steel) 1 and the composite material 2 are symmetrical (up and down in the figure) by the line of the release agent 4, and the spacers 5, 6 Are arranged so that the two laminated materials 2 and 2 and the release agent 4 can be contained within the thickness of. Thereafter, it is similarly assembled by welding in a vacuum. As shown, no dummy material is used in this case.
【００３６】さらに、いずれの場合も、母材（鋼）と合
わせ材との接合面には、いかなる中間材も介在させな
い。ただし、接合面は通常の方法で予め清浄化処理を施
しておく。Further, in any case, no intermediate material is interposed on the joint surface between the base material (steel) and the bonding material. However, the joint surface is previously subjected to a cleaning treatment by a normal method.
【００３７】合わせ材２としてはＴｉまたはＴｉ合金
（例えば、Ｔｉ−８％Ｍｎ、Ｔｉ−３％Ｃｒなど）を、
剥離剤４としてはＡｌ2 Ｏ3 を、ダミー材３とスペーサ
ー５、６としては母材と同じ鋼材を、それぞれ使用すれ
ばよい。As the bonding material 2, Ti or a Ti alloy (for example, Ti-8% Mn, Ti-3% Cr, etc.)
Al 2 O 3 may be used as the release agent 4, and the same steel material as the base material may be used as the dummy material 3 and the spacers 5 and 6.
【００３８】I.第１の方法 本発明の第１の方法は、上記のように組み立てた圧延用
スラブを既存の熱延設備を用いて、第１熱間圧延工程で
９５０〜１１００℃の温度範囲で圧下率１５％以上の圧
延を１パス以上施し、次いで第２熱間圧延工程で９００
℃〜６００℃の温度範囲で圧下率５％以上の圧延を１パ
ス以上施す連続圧延方法である。I. First Method In the first method of the present invention, the rolling slab assembled as described above is subjected to a temperature of 950 to 1100 ° C. in the first hot rolling step using existing hot rolling equipment. Rolling at a rolling reduction of 15% or more is performed in one pass or more in the range, and then 900 in the second hot rolling step.
This is a continuous rolling method in which rolling at a rolling reduction of 5% or more is performed in one or more passes in a temperature range of ℃ to 600 ° C.
【００３９】ただし、この第１の方法の第１熱間圧延工
程で望ましい圧下率の範囲は、母材鋼の炭素量が０．０
１mass％以下の場合には１５％以上４０％以下、次の第
２熱間圧延工程では５％以上４０％以下である。However, the range of the desired reduction in the first hot rolling step of the first method is that the carbon content of the base steel is 0.0%.
When it is 1 mass% or less, it is 15% or more and 40% or less, and in the next second hot rolling step, it is 5% or more and 40% or less.
【００４０】同じく、母材鋼の炭素量が上記０．０１ma
ss％を超え０．０５％以下の場合には、圧下率の範囲
は、第１熱間圧延工程では２０％以上、次の第２熱間圧
延工程では１０％以上である。Similarly, the carbon content of the base steel is 0.01 ma
When it exceeds ss% and is 0.05% or less, the range of the rolling reduction is 20% or more in the first hot rolling step and 10% or more in the next second hot rolling step.
【００４１】望ましい圧延パス数の上限は、いずれも６
〜２０パス程度である。The desired upper limit of the number of rolling passes is 6 in each case.
Approximately 20 passes.
【００４２】上記の限定理由および望ましい範囲の選択
理由を次に述べる。The reasons for the above limitation and the reasons for selecting the desired range will be described below.
【００４３】I-A.第１の方法の第１熱間圧延工程 第１熱間圧延工程において、圧延温度の下限を９５０℃
としたのは、最低温度が９５０℃であれば通常の鋼用の
熱延ライン設備をチタンクラッド鋼板圧延用に改造せず
に、そのまま使用することができるからである。一方、
上限を１１００℃としたのは、Ｔｉ−Ｆｅの二元系状態
図によると、Ｔｉ−３０mass％Ｆｅ程度の組成のＴｉ合
金では１０８５℃以上で溶融し始めることが示されてい
ることから、第１パス後の接合界面温度が１０８５℃よ
りも極端に高くならないようにするためである。IA. First Hot Rolling Step of First Method In the first hot rolling step, the lower limit of the rolling temperature is 950 ° C.
The reason for this is that if the minimum temperature is 950 ° C., ordinary hot-rolling line equipment for steel can be used as it is without modification for rolling titanium clad steel sheet. on the other hand,
The upper limit is set to 1100 ° C., since the binary phase diagram of Ti—Fe indicates that a Ti alloy having a composition of about Ti-30 mass% Fe starts to melt at 1085 ° C. or higher. This is for preventing the junction interface temperature after one pass from becoming extremely higher than 1085 ° C.
【００４４】第１熱間圧延工程の圧下率の範囲は、母材
鋼の炭素量が０．０１mass％を超え０．０５mass％以下
の場合には２０％以上、圧延パス数は１パス以上とす
る。母材鋼の炭素量が上記範囲で、圧下率が２０％未満
の場合には、形成される新生面での接合面積と比べ、金
属間化合物や炭化物を介した接合界面の面積が大きくな
り、合わせ材と鋼との接合強度が低くなる。このため、
圧延中に合わせ材と鋼がずれを生じ、クラッド鋼板の板
厚比のバラツキが大きくなり、健全なクラッド鋼板が得
られない。The range of the rolling reduction in the first hot rolling step is 20% or more when the carbon content of the base steel is more than 0.01 mass% and 0.05 mass% or less, and the number of rolling passes is 1 or more. I do. When the carbon content of the base steel is within the above range and the rolling reduction is less than 20%, the area of the bonding interface via the intermetallic compound or carbide becomes larger than the bonding area on the newly formed surface, and The joining strength between the material and steel decreases. For this reason,
During the rolling, a gap occurs between the laminated material and the steel, the variation in the thickness ratio of the clad steel sheet increases, and a sound clad steel sheet cannot be obtained.
【００４５】母材鋼の炭素量が０．０１mass％を超え
０．０５％以下の場合の圧下率の上限は、圧延ミルのパ
ワーおよび圧延用組立スラブの組立強度（圧延中にこの
スラブの先端部の溶接部が剥離しないこと）によって決
まるため、特に限定されず、連続的な圧下が可能な範囲
であればよい。When the carbon content of the base steel is more than 0.01 mass% and less than 0.05%, the upper limit of the rolling reduction is determined by the power of the rolling mill and the assembling strength of the assembling slab for rolling (the tip of this slab during rolling). Is not particularly limited, as long as it can be continuously reduced.
【００４６】上記条件では、圧延パス数は少なくとも１
パスで十分接合するが、望ましい上限は２０パス程度で
ある。Under the above conditions, the number of rolling passes is at least one.
Passing is sufficient for joining, but a desirable upper limit is about 20 passes.
【００４７】第１熱間圧延工程では、母材鋼の炭素量が
０．０１mass％以下の場合には、接合界面でのＴｉＣ炭
化物の形成を抑制することができるため、圧下率の下限
は、１５％に低下させることが可能となる。圧延パス数
は前記と同様の理由で１パス以上とする。In the first hot rolling step, when the carbon content of the base steel is 0.01 mass% or less, the formation of TiC carbide at the joint interface can be suppressed. It can be reduced to 15%. The number of rolling passes is one or more for the same reason as described above.
【００４８】母材鋼の炭素量が０．０１mass％以下の場
合の圧下率の上限は、圧延ミルのパワーと圧延用スラブ
の圧延形状（圧延中にこのスラブの溶接部が剥離せずに
正常に圧延されること）によって決まり、この観点から
４０％とするのが望ましい。When the carbon content of the base steel is 0.01 mass% or less, the upper limit of the rolling reduction is determined by the power of the rolling mill and the rolling shape of the slab for rolling (the welded portion of the slab does not peel off during rolling. To be rolled to about 40%), and from this viewpoint, it is desirable to set it to 40%.
【００４９】I-B.第１の方法の第２熱間圧延工程 本発明の第１の方法では、上記の条件で第１熱間圧延工
程を行い、引き続く第２熱間圧延工程で９００℃〜６０
０℃の温度範囲で圧下率５％以上の圧延を１パス以上施
す。IB. Second Hot Rolling Step of First Method In the first method of the present invention, the first hot rolling step is performed under the above conditions, and the subsequent second hot rolling step is performed at 900 ° C. to 60 ° C.
Rolling with a rolling reduction of 5% or more is performed in a temperature range of 0 ° C. for one or more passes.
【００５０】ただし、このときの望ましい圧下率は、母
材鋼の炭素量が０．０１mass％以下の場合には、５％以
上４０％以下である。同じく、母材鋼の炭素量が０．０
１mass％を超え０．０５mass％以下の場合には、１０％
以上である。However, the desirable rolling reduction at this time is 5% or more and 40% or less when the carbon content of the base steel is 0.01 mass% or less. Similarly, the carbon content of the base steel is 0.0
10% if more than 1 mass% and less than 0.05 mass%
That is all.
【００５１】スラブの圧延温度の下限を６００℃とした
のは、既存の鋼用圧延ミルがミルパワーや熱延条件を考
慮して、圧延最低温度を６００℃としているためであ
る。一方、圧延温度を９００℃以下とすれば、ＴｉＣ、
Ｔｉ−Ｆｅ、Ｔｉ−Ｆｅ2 等の接合強度に悪影響を及ぼ
す炭化物や金属間化合物の成長が遅くなり、接合強度の
低下が軽減される。The lower limit of the slab rolling temperature is set to 600 ° C. because the existing steel rolling mill sets the minimum rolling temperature to 600 ° C. in consideration of mill power and hot rolling conditions. On the other hand, if the rolling temperature is 900 ° C. or less, TiC,
Growth of Ti-Fe, Ti-Fe adversely affects carbide or intermetallic compound in the bonding strength, such as 2 becomes slow, deterioration in bonding strength is reduced.
【００５２】圧下率は、母材鋼の炭素量が０．０１mass
％以下の場合には、炭素量が低いためＴｉＣ炭化物の形
成を抑制することができ、５％でも十分な接合強度を確
保することができる。母材鋼の炭素量が０．０１mass％
を超える場合には、ＴｉＣ炭化物が形成されるので、こ
の炭化物を破壊するために、圧下率を１０％以上にしな
いと十分な接合強度が確保できなくなる。ただし、母材
鋼の炭素量が０．０５mass％を超えると、更にＴｉＣ炭
化物の形成が促進され、接合強度が低下する。The rolling reduction is such that the carbon content of the base steel is 0.01 mass
% Or less, the formation of TiC carbide can be suppressed because the carbon content is low, and sufficient bonding strength can be ensured even with 5%. The carbon content of the base steel is 0.01 mass%
If Ti exceeds 3, a TiC carbide will be formed. Therefore, in order to break the carbide, unless the rolling reduction is set to 10% or more, sufficient bonding strength cannot be secured. However, when the carbon content of the base steel exceeds 0.05 mass%, the formation of TiC carbide is further promoted, and the joining strength is reduced.
【００５３】圧下率の上限については、前述と同様の理
由によって決まるため、母材鋼の炭素量が０．０１mass
％以下の場合には４０％とするのが望ましい。一方、母
材鋼の炭素量が０．０１mass％を超え０．０５mass％以
下の場合には、前述と同様に、圧下率の上限は特に限定
されず、連続的な圧下が可能な範囲であればよい。Since the upper limit of the rolling reduction is determined for the same reason as described above, the carbon content of the base steel is 0.01 mass
%, It is desirably 40%. On the other hand, when the carbon content of the base steel is more than 0.01 mass% and not more than 0.05 mass%, the upper limit of the rolling reduction is not particularly limited, as described above, as long as continuous rolling can be performed. I just need.
【００５４】次に、合わせ材をＴｉ、母材を炭素量が
０．０１mass％を超え０．０５mass％以下の鋼とし、圧
下率を第１熱間圧延で２０％以上、第２熱間圧延で１０
％以上とした場合を例にとって、本発明方法の作用効果
を詳述する。Next, the joining material is Ti, the base material is steel having a carbon content of more than 0.01 mass% and not more than 0.05 mass%, the rolling reduction is 20% or more in the first hot rolling, and the second hot rolling is At 10
%, The operation and effect of the method of the present invention will be described in detail.
【００５５】本発明方法のように、第１熱間圧延で９５
０℃以上、圧下率２０％以上で圧延した場合、第１パス
目の圧下により、高い温度でＴｉと母材鋼が接触、接合
することとなり、当然圧延温度が高いために、その界面
の一部には脆弱な金属間化合物および炭化物が形成さ
れ、Ｔｉ／金属間化合物および炭化物／鋼の界面と、Ｔ
ｉ／鋼の界面とを有するスラブとなる。しかし、圧下率
が２０％以上と大きい場合には、新生面の割合が大きく
なるため、母材鋼とＴｉのずれを生じることなく、次の
第２熱間圧延工程における圧延が可能となる。一方、第
１熱間圧延で圧下率が２０％未満の場合には、Ｔｉと母
材鋼の圧接が不十分なため、新生面による接合面積が相
対的に小さく、圧延中にＴｉと鋼のずれを生じてＴｉと
鋼の板厚比のバラツキが大きくなり、健全なチタンクラ
ッド鋼板が得られない。As in the method of the present invention, 95% is used in the first hot rolling.
When the rolling is performed at 0 ° C. or more and the rolling reduction is 20% or more, the rolling of the first pass causes the Ti and the base steel to contact and join at a high temperature, and naturally the rolling temperature is high. A brittle intermetallic compound and carbide are formed in the portion, and the Ti / intermetallic compound and carbide / steel interface and T
A slab having an i / steel interface. However, when the rolling reduction is as large as 20% or more, the ratio of the new surface becomes large, so that the rolling in the next second hot rolling step can be performed without a shift between the base steel and Ti. On the other hand, when the rolling reduction is less than 20% in the first hot rolling, the pressure contact between Ti and the base material steel is insufficient, so that the joining area due to the new surface is relatively small, and the displacement between Ti and the steel during rolling is small. As a result, the variation in the thickness ratio between Ti and steel becomes large, and a sound titanium clad steel sheet cannot be obtained.
【００５６】さらに、このスラブに圧下率２０％以上の
第２パス以降の圧下を行った場合（第１熱間圧延工程に
おいて連続圧下をする場合）でも、Ｔｉや母材鋼と比
べ、極端に変形能の小さい金属間化合物および炭化物
は、Ｔｉや母材鋼の変形に追随することができずに割
れ、結果として界面の金属間化合物および炭化物の厚さ
が小さくなるとともに、圧延変形によりＴｉと母材鋼の
新生面が形成され、これらの面同志が接合されるため
に、圧延中に母材鋼とＴｉのずれを生じることなく連続
圧下が可能となる。Further, even when the slab is subjected to the second and subsequent reductions with a reduction rate of 20% or more (in the case of continuous reduction in the first hot rolling step), the slab is extremely extremely reduced in comparison with Ti and base steel. Intermetallic compounds and carbides with low deformability cannot crack Ti or the deformation of the base steel and cannot be deformed.As a result, the thickness of intermetallic compounds and carbides at the interface is reduced, and Ti and Ti are reduced by rolling deformation. Since a new surface of the base steel is formed and these surfaces are joined to each other, continuous rolling can be performed without causing a shift between the base steel and Ti during rolling.
【００５７】このように、９５０℃以上で圧下率２０％
以上の圧延を行う第１熱間圧延工程では、新生面での接
合と金属間化合物および炭化物の形成、成長が繰り返さ
れることとなり、これらの工程で得られたチタンクラッ
ド鋼板のスラブには、当然、接合界面に金属間化合物お
よび炭化物を有することとなるが、圧下率が２０％以上
と大きく、母材鋼とＴｉが強固に圧着されているため
に、圧延中に母材鋼とＴｉのずれを生じることなく、圧
下を行うことができる。As described above, at a temperature of 950 ° C. or more, the rolling reduction is 20%.
In the first hot rolling step of performing the above rolling, the joining on the new surface and the formation and growth of intermetallic compounds and carbides are repeated, and the slab of the titanium clad steel sheet obtained in these steps is, of course, Although it has intermetallic compounds and carbides at the joint interface, the reduction ratio is as large as 20% or more, and the base material steel and Ti are firmly pressed together. The reduction can be performed without any occurrence.
【００５８】さらに、スラブを６００〜９００℃の温度
で、圧下率１０％以上の少なくとも１パスの第２熱間圧
延を行えば、新たに上記のように新生面でのＴｉと母材
鋼の接合が起こることに加えて、圧延温度が低いため
に、界面の金属間化合物および炭化物の形成、成長が小
さく、高い接合強度を有するチタンクラッド鋼板を得る
ことができる。Further, when the slab is subjected to at least one pass of the second hot rolling at a temperature of 600 to 900 ° C. and a rolling reduction of 10% or more, the joining of Ti and the base material steel on the newly formed surface is newly performed as described above. In addition to the fact that the rolling temperature is low, the formation and growth of intermetallic compounds and carbides at the interface are small, and a titanium clad steel sheet having high bonding strength can be obtained.
【００５９】通常の熱間圧延によるチタンクラッド鋼板
の製造は、第２熱間圧延工程のみで十分に可能である
が、既存の鋼用の熱延設備を用いて安価なチタンクラッ
ド鋼板を製造するためには、鋼の熱延ラインの加熱温度
と同等の１０００℃前後まで、圧延用スラブを加熱する
ことが必要となる。そこで、高い温度での連続的な圧下
を可能にし、多量のクラッド鋼板を製造するためには、
大きな圧下率（２０％以上）で圧延する本発明方法の中
にあるような第１熱間圧延工程が必要となる。The production of a titanium clad steel sheet by ordinary hot rolling can be sufficiently performed only by the second hot rolling step, but an inexpensive titanium clad steel sheet is produced by using existing hot rolling equipment for steel. For this purpose, it is necessary to heat the rolling slab to about 1000 ° C., which is equivalent to the heating temperature of the steel hot rolling line. Therefore, in order to enable continuous reduction at high temperature and to produce a large amount of clad steel sheet,
The first hot rolling step as in the method of the present invention for rolling at a large rolling reduction (20% or more) is required.
【００６０】II. 第２の方法 本発明の第２の方法は、第１の方法の第１熱間圧延工程
の後、スラブをいったん９００℃以下まで放冷し、その
後第１の方法の第２熱間圧延工程を施すものである。II. Second Method In the second method of the present invention, after the first hot rolling step of the first method, the slab is once cooled to 900 ° C. or less, and then the first method is used. (2) A hot rolling step is performed.
【００６１】Ｔｉは昇温すると約９００℃でαからβに
変態し、原子の充填率の高い六方晶系から、充填率の低
い立方晶系の結晶構造となる。このため、α−Ｔｉ中の
Ｆｅ原子の拡散速度は、β−Ｔｉ中の拡散速度に比べて
約１０倍程度遅くなり、ＦｅとＴｉとの界面における金
属間化合物の形成が抑制される。すなわち、第１熱間圧
延工程後、スラブを放冷して９００℃以下にし、確実に
９００〜６００℃のα−Ｔｉの温度領域内で第２熱間圧
延を行うことにより、さらに接合強度の高いチタンクラ
ッド鋼板を得ることができる。望ましい放冷温度の下限
は７００℃である。When the temperature rises, Ti transforms from α to β at about 900 ° C., and changes from a hexagonal system with a high atomic filling factor to a cubic system with a low atomic filling factor. For this reason, the diffusion rate of Fe atoms in α-Ti is about 10 times slower than the diffusion rate in β-Ti, and the formation of intermetallic compounds at the interface between Fe and Ti is suppressed. That is, after the first hot rolling step, the slab is allowed to cool to 900 ° C. or lower, and the second hot rolling is performed reliably within the temperature range of α-Ti of 900 to 600 ° C., thereby further increasing the bonding strength. A high titanium clad steel sheet can be obtained. The lower limit of the desirable cooling temperature is 700 ° C.
【００６２】[0062]
【実施例】母材鋼として、Ｃ：０．０３mass％、板厚８
０ｍｍの炭素鋼と、Ｃ：０．０１mass％以下、板厚８０
ｍｍの極低炭素鋼、合わせ材として板厚２０ｍｍの純チ
タン（JIS H4600、１種）を用いて、図３に示す非対称
型、対称型の圧延用スラブを真空中（１０-2Torr以下）
溶接で組み立てた。剥離剤としてＡｌ2 Ｏ3 を塗布し、
ダミー材およびスペーサーとしては、それぞれ母材と同
じ鋼材を使用した。EXAMPLES As base metal, C: 0.03 mass%, plate thickness 8
0 mm carbon steel, C: 0.01 mass% or less, plate thickness 80
mm, ultra-low carbon steel and pure titanium (JIS H4600, 1 type) with a thickness of 20 mm as a joining material, and asymmetrical and symmetrical rolling slabs shown in FIG. 3 in vacuum (10 -2 Torr or less)
Assembled by welding. Al 2 O 3 is applied as a release agent,
The same steel material as the base material was used for each of the dummy material and the spacer.
【００６３】次いで、表１および表２に示す圧延条件に
従い、圧延用モデルミルを用いて非対称型圧延用スラブ
から板厚６．５ｍｍ（ダミー材厚を含む。クラッド鋼板
厚は５ｍｍ。ただし、 steel：Ti＝４：１）の、対称型
スラブから板厚１０ｍｍの、それぞれチタンクラッド鋼
板を製造し、連続圧下性をシャー切断による切断部のク
ラッド界面の剥離（開口）の有無（有り：×、なし：
○）により評価した。これらの結果を表１および表２に
併せて示す。Next, according to the rolling conditions shown in Tables 1 and 2, a plate thickness of 6.5 mm (including a dummy material thickness. The thickness of a clad steel plate is 5 mm. : Ti = 4: 1), a titanium-clad steel sheet having a thickness of 10 mm was manufactured from a symmetrical slab, and the continuous rolling property was checked for the presence or absence of peeling (opening) of the clad interface of the cut portion by shear cutting (available: ×, None:
○). The results are shown in Tables 1 and 2.
【００６４】[0064]
【表１】 [Table 1]
【００６５】[0065]
【表２】 [Table 2]
【００６６】表１および表２に示すように、第１熱間圧
延工程の圧下率が、母材鋼のＣ濃度が０．０３mass％の
場合２０％未満、母材鋼のＣ濃度が０．０１mass％以下
の場合１５％未満であると、圧延中にチタンと母材鋼と
のずれが生じ、クラッド鋼板の板厚比のバラツキが大き
くなり、健全なチタンクラッド鋼板は得られなかった。 As shown in Tables 1 and 2, the first hot pressure
The rolling reduction of the rolling process is such that the C concentration of the base steel is 0.03 mass%.
In case of less than 20%, C concentration of base steel is less than 0.01 mass%
In the case of less than 15% , the displacement between titanium and the base steel occurred during rolling, the variation in the thickness ratio of the clad steel plate increased, and a sound titanium clad steel plate was not obtained.
【００６７】また、第２熱間圧延工程の圧下率が、母材
鋼のＣ濃度が０．０３mass％の場合１０％未満、母材鋼
のＣ濃度が０．０１mass％以下の場合５％未満であった
り、この工程で定めた適正温度範囲で圧延を行わなかっ
た場合には、シャー切断により切断部の剥離を生じ、高
い接合強度を有するチタンクラッド鋼板は得られなかっ
た。[0067] Further, reduction rate of the second hot rolling step, the base material
Less than 10% when C concentration of steel is 0.03 mass%, base metal
Was less than 5% when the C concentration was 0.01 mass% or less.
In contrast, when rolling was not performed within the appropriate temperature range determined in this step, the cut portion was peeled off by shear cutting, and a titanium clad steel sheet having high bonding strength was not obtained.
【００６８】[0068]
【００６９】第１熱間圧延工程の圧延温度の最低値が９
５０℃を、または第２熱間圧延工程の圧延温度の最低値
が６００℃を、それぞれ下まわると、圧下の困難や界面
の剥離が生じた。The minimum value of the rolling temperature in the first hot rolling step is 9
When the rolling temperature in the second hot rolling step was lower than 50 ° C. or 600 ° C., respectively, it was difficult to reduce the pressure and peeling of the interface occurred.
【００７０】[0070]
【発明の効果】本発明方法により、従来の鋼用の熱延設
備を用いてチタンクラッド鋼板の大量生産を達成するこ
とが可能である。本発明方法では、圧下率が大きく、歩
留まりと接合強度が大幅に改善される。したがって、得
られるチタンクラッド鋼板は低コストであるとともに高
い接合強度を有するものである。According to the method of the present invention, it is possible to achieve mass production of titanium-clad steel sheets using conventional hot-rolling equipment for steel. In the method of the present invention, the rolling reduction is large, and the yield and the joining strength are greatly improved. Therefore, the obtained titanium clad steel sheet is low in cost and has high bonding strength.
【図１】接合強度に及ぼす圧延温度と圧下率との影響を
示す図である。FIG. 1 is a diagram showing the effects of rolling temperature and rolling reduction on bonding strength.
【図２】母材鋼の炭素量が０．０１mass％以下の場合の
接合強度に及ぼす圧延温度と圧下率との影響を示す図で
ある。FIG. 2 is a graph showing the effect of rolling temperature and rolling reduction on bonding strength when the carbon content of a base steel is 0.01 mass% or less.
【図３】圧延用スラブの組立後の断面を示す図であり、
(a) は非対称型スラブ、(b) は対称型スラブの場合であ
る。FIG. 3 is a view showing a cross section of the rolling slab after assembly.
(a) is for an asymmetric slab, and (b) is for a symmetric slab.
１：母材（鋼）、２：合わせ材（ＴｉまたはＴｉ合
金）、３：ダミー材、４：剥離剤、 ５，６：スペー
サー1: Base material (steel), 2: Laminated material (Ti or Ti alloy), 3: Dummy material, 4: Release agent, 5, 6: Spacer
───────────────────────────────────────────────────── フロントページの続き (56)参考文献 特開 昭62−93090（ＪＰ，Ａ) 特開 昭60−213378（ＪＰ，Ａ) 特開 昭56−122681（ＪＰ，Ａ) 特開 平４−118183（ＪＰ，Ａ) 特開 昭61−297135（ＪＰ，Ａ) (58)調査した分野(Int.Cl.7，ＤＢ名) B23K 20/00 - 20/26 ──────────────────────────────────────────────────続 き Continuation of the front page (56) References JP-A-62-93090 (JP, A) JP-A-60-213378 (JP, A) JP-A-56-122681 (JP, A) JP-A-4- 118183 (JP, A) JP-A-61-297135 (JP, A) (58) Fields investigated (Int. Cl. 7 , DB name) B23K 20/00-20/26
Claims (3)
鋼材、合わせ材としてチタンまたはチタン合金を用い、
母材と合わせ材の接合面を真空排気した後溶接して組み
立てた圧延用組立スラブを、熱間圧延により接合するチ
タンクラッド鋼板の製造方法であって、圧延用組立スラ
ブに第１熱間圧延工程で９５０〜１１００℃の温度範囲
で圧下率１５％以上の圧延を１パス以上施し、次いで第
２熱間圧延工程で９００℃〜６００℃の温度範囲で圧下
率５％以上の圧延を１パス以上施すことを特徴とするチ
タンクラッド鋼板の製造方法。1. A steel material having a carbon content of 0.01 mass% or less as a base material and titanium or a titanium alloy as a composite material.
A method for producing a titanium clad steel sheet by hot-rolling an assembly slab for rolling, which is assembled by evacuating and welding a joint surface between a base material and a joining material, wherein the first hot-rolling is performed on the assembly slab for rolling. In the process, rolling at a temperature range of 950 to 1100 ° C. is performed in one pass or more at a rolling reduction of 15% or more, and then in a second hot rolling process, rolling at a temperature range of 900 ° C. to 600 ° C. is performed in one pass at a rolling reduction of 5% or more. A method for producing a titanium clad steel sheet, which is performed as described above.
０．０５mass％以下の鋼材、合わせ材としてチタンまた
はチタン合金を用い、母材と合わせ材の接合面を真空排
気した後溶接して組み立てた圧延用組立スラブを、熱間
圧延により接合するチタンクラッド鋼板の製造方法であ
って、圧延用組立スラブに第１熱間圧延工程で９５０〜
１１００℃の温度範囲で圧下率２０％以上の圧延を１パ
ス以上施し、次いで第２熱間圧延工程で９００℃〜６０
０℃の温度範囲で圧下率１０％以上の圧延を１パス以上
施すことを特徴とするチタンクラッド鋼板の製造方法。 2. The base material has a carbon content exceeding 0.01 mass%.
0.05 mass% or less steel, titanium or titanium
Uses a titanium alloy and evacuates the joint surface between the base material and the mating material.
The rolling assembly slab assembled by welding after welding
A method of manufacturing a titanium clad steel sheet to be joined by rolling.
Thus, in the first hot rolling step, 950-
Rolling with a rolling reduction of 20% or more in a temperature range of 1100 ° C
And then in the second hot rolling step at 900 ° C to 60 ° C.
Rolling with a rolling reduction of 10% or more in a temperature range of 0 ° C for 1 pass or more
A method for producing a titanium-clad steel sheet, comprising:
に、被圧延材を９００℃以下まで放冷する放冷工程を介
在させることを特徴とする請求項１または２に記載のチ
タンクラッド鋼板の製造方法。 3. Between a first hot rolling step and a second hot rolling step.
Through a cooling step of cooling the material to be rolled to 900 ° C or less.
3. The switch according to claim 1, wherein
Manufacturing method of tan clad steel sheet.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP6283629A JP3047752B2 (en) | 1994-11-17 | 1994-11-17 | Manufacturing method of titanium clad steel sheet |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP6283629A JP3047752B2 (en) | 1994-11-17 | 1994-11-17 | Manufacturing method of titanium clad steel sheet |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH08141754A JPH08141754A (en) | 1996-06-04 |
| JP3047752B2 true JP3047752B2 (en) | 2000-06-05 |
Family
ID=17667995
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP6283629A Expired - Fee Related JP3047752B2 (en) | 1994-11-17 | 1994-11-17 | Manufacturing method of titanium clad steel sheet |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP3047752B2 (en) |
Families Citing this family (12)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO1999062665A1 (en) * | 1998-06-03 | 1999-12-09 | Sumitomo Special Metals Co., Ltd. | Clad material and method of manufacturing the material |
| US6716554B2 (en) | 1999-04-08 | 2004-04-06 | Quallion Llc | Battery case, cover, and feedthrough |
| CN102837463B (en) * | 2012-09-24 | 2014-07-30 | 辽宁新华阳伟业装备制造有限公司 | Rolled composite titanium-steel-titanium composite board and manufacturing method thereof |
| CN103817149A (en) * | 2014-03-13 | 2014-05-28 | 沈阳和世泰通用钛业有限公司 | Pack rolling production method of titanium steel composite board |
| CN107847994B (en) | 2015-07-29 | 2020-03-13 | 日本制铁株式会社 | Titanium composite material and titanium material for hot rolling |
| TWI637065B (en) | 2015-07-29 | 2018-10-01 | 日商新日鐵住金股份有限公司 | Titanium composite and titanium for hot work |
| CN105234177A (en) * | 2015-09-30 | 2016-01-13 | 北京科技大学 | Hot rolling method for restraining warping of asymmetrically-assembled titanium steel composite board |
| CN113145667A (en) * | 2021-05-10 | 2021-07-23 | 成都先进金属材料产业技术研究院股份有限公司 | Continuous furnace high-temperature heating method for TA titanium and Q235 steel composite board/coiled raw material blank |
| CN113145665A (en) * | 2021-05-10 | 2021-07-23 | 成都先进金属材料产业技术研究院股份有限公司 | Chamber furnace isothermal heating method of TA titanium and Q235 steel composite board/coiled raw material blank |
| CN113145663A (en) * | 2021-05-10 | 2021-07-23 | 成都先进金属材料产业技术研究院股份有限公司 | Chamber furnace heating method for TA titanium and Q235 steel composite board/coiled raw material blank |
| CN113145666A (en) * | 2021-05-10 | 2021-07-23 | 成都先进金属材料产业技术研究院股份有限公司 | Continuous furnace isothermal heating method for TA titanium and Q235 steel composite plate/coiled stock blank |
| CN115041523A (en) * | 2022-06-30 | 2022-09-13 | 湖南湘投金天钛金属股份有限公司 | Method for preparing wide titanium alloy plate by adopting titanium steel combined mode |
-
1994
- 1994-11-17 JP JP6283629A patent/JP3047752B2/en not_active Expired - Fee Related
Also Published As
| Publication number | Publication date |
|---|---|
| JPH08141754A (en) | 1996-06-04 |
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