JPH04143236A - High strength alpha type titanium alloy excellent in cold workability - Google Patents
High strength alpha type titanium alloy excellent in cold workabilityInfo
- Publication number
- JPH04143236A JPH04143236A JP26377790A JP26377790A JPH04143236A JP H04143236 A JPH04143236 A JP H04143236A JP 26377790 A JP26377790 A JP 26377790A JP 26377790 A JP26377790 A JP 26377790A JP H04143236 A JPH04143236 A JP H04143236A
- Authority
- JP
- Japan
- Prior art keywords
- titanium alloy
- cold
- type titanium
- high strength
- alpha type
- 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
- 229910001069 Ti alloy Inorganic materials 0.000 title abstract description 13
- 239000010936 titanium Substances 0.000 claims abstract description 15
- 229910052719 titanium Inorganic materials 0.000 claims abstract description 12
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 claims description 10
- 239000000956 alloy Substances 0.000 claims 1
- 229910045601 alloy Inorganic materials 0.000 claims 1
- 229910052804 chromium Inorganic materials 0.000 abstract description 4
- 229910052742 iron Inorganic materials 0.000 abstract description 4
- 229910052720 vanadium Inorganic materials 0.000 abstract description 4
- 229910052759 nickel Inorganic materials 0.000 abstract description 3
- 150000003608 titanium Chemical class 0.000 abstract 1
- 238000005336 cracking Methods 0.000 description 7
- 239000000463 material Substances 0.000 description 5
- 238000005452 bending Methods 0.000 description 3
- 239000000203 mixture Substances 0.000 description 3
- 238000005097 cold rolling Methods 0.000 description 2
- 230000007547 defect Effects 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 238000004519 manufacturing process Methods 0.000 description 2
- 238000005096 rolling process Methods 0.000 description 2
- 229910017709 Ni Co Inorganic materials 0.000 description 1
- 238000000137 annealing Methods 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- 230000001771 impaired effect Effects 0.000 description 1
- 238000003754 machining Methods 0.000 description 1
- 238000005259 measurement Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 239000007769 metal material Substances 0.000 description 1
- 238000005204 segregation Methods 0.000 description 1
- 230000000087 stabilizing effect Effects 0.000 description 1
- 238000009864 tensile test Methods 0.000 description 1
Landscapes
- Electrodes For Cathode-Ray Tubes (AREA)
Abstract
Description
【発明の詳細な説明】
[産業上の利用分野]
この発明は、高強度を有するのみならず、冷間成形性に
も優れ、例えば熱交換器用パイプ、自動車や航空機用の
パネル部品等の冷間加工用製造素材として好適なα型チ
タン合金に関する。Detailed Description of the Invention [Industrial Application Field] The present invention not only has high strength but also has excellent cold formability, and is suitable for use in cold forming, for example, pipes for heat exchangers, panel parts for automobiles and aircraft, etc. The present invention relates to an α-type titanium alloy suitable as a manufacturing material for machining.
[従来の技術及び発明が解決しようとする課題]チタン
は耐食性に優れていることから従来より熱交換器パイプ
に多用されてきている。純チタンは冷間加工性か良好で
あることから、この熱交換器用パイプは純チタン冷間圧
延板をパイプ成形することにより製造される。また、こ
のような良好な冷間加工性により、純チタンはパネル部
品等にも用いられてきている。しかしながら、このよう
な用途に適用される純チタン薄板は、特に加工性が良好
なJ 131種、2種であるか、これらは0.2%耐力
が低く、この値が高いほうのJIS2種でも得られる0
、2%耐力は高々30 kg/■膳2にすぎない。現在
、熱交換器用パイプには0.7■材が多用されているが
、熱交換率を上昇させるためにさらに薄肉化を図ること
が要望されており、上述のような純チタンの強度では不
十分である。[Prior Art and Problems to be Solved by the Invention] Titanium has been widely used for heat exchanger pipes since it has excellent corrosion resistance. Since pure titanium has good cold workability, this heat exchanger pipe is manufactured by pipe-forming a pure titanium cold-rolled plate. Moreover, due to such good cold workability, pure titanium has been used for panel parts and the like. However, the pure titanium thin sheets used for such applications are either J131 type or J2 type, which have particularly good workability, or they have a low 0.2% proof stress, and even JIS type 2, which has a higher value, cannot be used. 0 obtained
, the 2% yield strength is only 30 kg/2 pieces at most. Currently, 0.7mm material is often used for heat exchanger pipes, but there is a demand for thinner walls to increase the heat exchange efficiency, and the strength of pure titanium as described above is insufficient. It is enough.
方、チタン合金は実用金属材料中で最も高い比強度を有
することから、これまで特に航空機部品として多用され
てきているが、近年これら用途のみならず一般産業用途
への応用も検討されている。しかしながら、チタン合金
は純チタンと比較して強度は優れているものの、一般に
は冷間圧延性、冷間成形性が悪く、従ってその改善がチ
タン合金の用途拡大にあたって大きな課題となっている
。一般に、冷間成形では種々の欠陥が現れるが、チタン
合金の冷間成形では「割れ」、そして割れが生じない場
合には「ゴーストライン」と称する欠陥の発生が問題と
なる。ゴーストラインが発生すると外観が著しく損なわ
れ商品価値か低下するのみならず、板厚が不均一となり
このため製品の強度不良をもたらしてしまう。On the other hand, titanium alloys have the highest specific strength among practical metal materials, and have thus far been used extensively, especially as aircraft parts, but in recent years, their application not only to these uses but also to general industrial uses has been considered. However, although titanium alloys have superior strength compared to pure titanium, they generally have poor cold rollability and cold formability, and therefore, improving these properties is a major issue in expanding the use of titanium alloys. In general, various defects appear during cold forming, but cold forming of titanium alloys causes problems such as "cracks" and, when no cracks occur, the occurrence of defects called "ghost lines." When ghost lines occur, not only the appearance is significantly impaired and the commercial value is reduced, but also the plate thickness becomes uneven, resulting in poor strength of the product.
この発明はかかる事情に鑑みてなされたものであって、
0.2%耐力が30 kg/ 112以上であり、かつ
冷間成形時に割れ及びゴーストラインの発生のない冷間
成形性に優れたα型チタン合金を提供することを目的と
する。This invention was made in view of such circumstances, and
The object of the present invention is to provide an α-type titanium alloy having a 0.2% yield strength of 30 kg/112 or more and excellent cold formability without cracking or ghost lines during cold forming.
[課題を解決するための手段]
この発明に係る冷間成形性に優れた高強度α型チタン合
金は、重量%で、(V/13)+(Fe/20) +(
Cr/17) 十(Ni/31)+(Co/23)が0
.10%以下であり、かつO≦0.6%、11≦4.0
%、及び(5/2)0+ (1/3)AI≧0.90%
を満たす範囲で0及びAIを含み、残部が実質的にTi
からなることを特徴とする。[Means for Solving the Problems] The high-strength α-type titanium alloy with excellent cold formability according to the present invention has the following composition (V/13) + (Fe/20) + (in weight %).
Cr/17) Ten (Ni/31) + (Co/23) is 0
.. 10% or less, and O≦0.6%, 11≦4.0
%, and (5/2)0+ (1/3)AI≧0.90%
0 and AI within the range that satisfies the requirements, and the remainder is substantially Ti.
It is characterized by consisting of.
なお、以下簡略のため(V/13)+ (Fe/20)
+ (Cr/17)+ (Ni/31)+(Co /
23 )をEQIで表す。In addition, for the sake of simplicity, (V/13) + (Fe/20)
+ (Cr/17)+ (Ni/31)+(Co/
23) is expressed as EQI.
[作用]
本発明者等は、成形加工用チタン合金薄板の冷間成形時
におけるゴーストラインの発生を抑えるべく研究・検討
した結果、チタンにおけるβ安定元素であるV、Fe、
Cr、Ni、Coの含有量を一定値以下に制御すること
によりゴーストラインの発生が防止されることを新たに
見出した。[Function] As a result of research and consideration in order to suppress the generation of ghost lines during cold forming of titanium alloy thin sheets for forming processing, the present inventors found that V, Fe, which are β-stable elements in titanium,
It has been newly discovered that the generation of ghost lines can be prevented by controlling the contents of Cr, Ni, and Co to below a certain value.
ココでV、Fe、Cr、Ni、Coの含有量がEQI>
0.10重量%の関係にある場合にゴストラインの発生
が認められる。これはβ安定化元素の含有量が多い場合
、どうしても製造履歴に起因してこれらβ安定化元素の
偏析を生し、その結果硬度の異なるα晶、3品が不均一
に混在したミクロ組織が冷間成形素材に生じるためであ
る。The content of V, Fe, Cr, Ni, and Co here is EQI>
When the relationship is 0.10% by weight, the occurrence of ghost lines is observed. This is because when the content of β-stabilizing elements is high, segregation of these β-stabilizing elements inevitably occurs due to the manufacturing history, resulting in a microstructure in which three types of α-crystals with different hardness are mixed unevenly. This is because it occurs in cold-formed materials.
従ってEQI≦0.10重量%に規定する。なお、これ
らβ安定化元素の作用の割合は、V:Fe:Cr:Ni
:Co=1/13:1/20:1/17 : 1/31
: 1/23であるため、これらの含有量を上述のE
QIて規定した。Therefore, it is specified that EQI≦0.10% by weight. Note that the ratio of the effects of these β stabilizing elements is V:Fe:Cr:Ni
:Co=1/13:1/20:1/17:1/31
: Since it is 1/23, these contents are calculated as E above.
QI was specified.
一方、i及びOは、チタンに添加されることにより高強
度を達成する元素である。しかしなから、これらが夫々
4,0重量%及び0.6重量%を超えると高強度化は達
成されるものの冷延性が低下する。従って、Alを4.
0重1%以下、0を0.6重量%以下に規定する。また
、AI及び0の含有量が、(5/2)O+ (1/3)
AI <0.90重量%である場合には、目標とする3
0kg/■■2以上の0,2%耐力が得られないため、
(5/2)O+ (1/3)AI! ≧0.90重量%
に規定する。On the other hand, i and O are elements that achieve high strength by being added to titanium. However, if these amounts exceed 4.0% by weight and 0.6% by weight, respectively, although high strength is achieved, cold rollability deteriorates. Therefore, 4.
Zero weight is defined as 1% or less, and 0 is defined as 0.6 weight% or less. Also, the content of AI and 0 is (5/2)O+ (1/3)
If AI <0.90 wt%, target 3
Since 0.2% yield strength of 0kg/■■2 or more cannot be obtained,
(5/2) O+ (1/3) AI! ≧0.90% by weight
stipulates.
[実施例] 以下、この発明の実施例について説明する。[Example] Examples of the present invention will be described below.
第1表に示されているような成分組成のインゴット(番
号1〜82)をVAR溶解によって製造し、1000℃
にて熱間鍛造して厚さ16m5のスラブとした。次にこ
れらスラブを80[)℃で熱間圧延し、板厚311の熱
延板に仕上げた。そして、これら熱延板をコイルグライ
ンダーによりスケール除去し、板厚2.21の冷間圧延
素材とした。Ingots (numbers 1 to 82) having the composition shown in Table 1 were produced by VAR melting, and heated to 1000°C.
It was hot forged into a slab with a thickness of 16m5. Next, these slabs were hot-rolled at 80[)° C. to produce a hot-rolled plate having a thickness of 311 mm. Then, scale was removed from these hot-rolled plates using a coil grinder to obtain a cold-rolled material having a plate thickness of 2.21 mm.
その後50%の冷間圧延を施して冷間圧延後の割れの発
生の有無を目視により検査した。第1表には、この割れ
の発生の有無を0(割れの発生無し)及び×(割れの発
生有り)で示した。さらに割れの発生が認められなかっ
た冷間圧延材に650℃で1時間の真空焼鈍を施し、そ
の機械的性質とゴーストラインの発生状況とを調査した
。機械的性質は、圧延方向に平行にJIS 13B試
験片(平行部:12.5−一、GL:50濡I)を採取
し、この試験片を引張試験に供してその0.2%耐力を
測定することによって把握した。また、ゴーストライン
の発生は、圧延直角方向に採取した曲げ試験片を用い、
曲げ半径20T(T:板厚)の曲げ試験を行い、ゴース
トラインの発生の有無を目視により判定した。第1表に
は、ゴーストラインの発生の有無をO(ゴーストライン
の発生無し)及び×(ゴーストラインの発生有り)で示
した。Thereafter, it was cold rolled by 50% and visually inspected for the occurrence of cracks after cold rolling. In Table 1, the presence or absence of cracking is indicated by 0 (no cracking) and x (cracking). Furthermore, the cold-rolled material in which no cracking was observed was subjected to vacuum annealing at 650° C. for 1 hour, and its mechanical properties and the occurrence of ghost lines were investigated. Mechanical properties were determined by taking a JIS 13B test piece (parallel part: 12.5-1, GL: 50 wet I) parallel to the rolling direction, and subjecting this test piece to a tensile test to determine its 0.2% yield strength. This was determined through measurement. In addition, the occurrence of ghost lines was investigated using bending test pieces taken in the direction perpendicular to rolling.
A bending test was conducted with a bending radius of 20T (T: plate thickness), and the presence or absence of ghost lines was visually determined. In Table 1, the presence or absence of ghost lines is indicated by O (ghost lines not occurring) and × (ghost lines occurring).
第1表にはこれらの試験結果を示す。また、Al及びO
の含有量と特性との関係を第1図に示す。Table 1 shows the results of these tests. Also, Al and O
The relationship between the content and properties is shown in Figure 1.
先ず、V、Fe、Cr、Ni Coについては、第1
表に示すように、EQIか0.10%(重量%表示、以
下同様)を超えるとゴーストラインか発生することが確
認された。First, for V, Fe, Cr, and Ni Co, the first
As shown in the table, it was confirmed that ghost lines were generated when EQI exceeded 0.10% (expressed as weight %, hereinafter the same).
次に、AΩ及びOについては、第1表及び第1図に示す
ように、Ajll>4.0%、O> 0 、 696て
冷間割れが発生することが確認された。一方、(5/2
)O+ (1/3)Al <0.90%の範囲では0.
2%耐力が30 kg/ as2未満と低い値であるこ
とが確認された。Next, regarding AΩ and O, as shown in Table 1 and FIG. 1, it was confirmed that cold cracking occurs when Ajll>4.0%, O>0, and 696. On the other hand, (5/2
)O+ (1/3)Al 0.0% in the range <0.90%.
It was confirmed that the 2% proof stress was a low value of less than 30 kg/as2.
これに対し、EQ1≦0,10%で、かつ0≦0.6%
、AI?≦4,0%、(5/2)O+(1/3)All
≧0.9%である本発明の範囲内の組成のものは、冷間
圧延時に割れか発生せず、またゴーストラインの発生も
認められなかった。On the other hand, when EQ1≦0.10% and 0≦0.6%
, AI? ≦4,0%, (5/2)O+(1/3)All
For those having a composition within the range of the present invention, which is ≧0.9%, only cracks occurred during cold rolling, and no ghost lines were observed.
さらに、 0゜ 2%耐力が30 kg/■12 以上と良好 な強度を示した。moreover, 0° 2% yield strength is 30 kg/■12 Good as above It showed great strength.
〔発明の効果]
この発明によれば、0,2%耐力が30 kg/−12
以上と良好な強度を示し、かつ冷間成形時に割れ及びゴ
ーストラインが発生しない冷間成彩性にすぐれたすぐれ
たα型チタン合金を提供することができる。[Effect of the invention] According to this invention, the 0.2% yield strength is 30 kg/-12
As described above, it is possible to provide an α-type titanium alloy that exhibits good strength and has excellent cold forming properties without cracking or ghost lines during cold forming.
第1図はチタン合金におけるAl及び0の含有量と特性
との関係を示す図である。FIG. 1 is a diagram showing the relationship between the content of Al and 0 in a titanium alloy and its properties.
Claims (1)
7)+(Ni/31)+(Co/23)が0.10%以
下であり、かつO≦0.6%、Al≦4.0%、及び(
5/2)O+(1/3)Al≧0.90%を満たす範囲
でO及びAlを含み、残部が実質的にTiからなること
を特徴とする冷間成形性に優れた高強度αチタン合金。In weight%, (V/13) + (Fe/20) + (Cr/1
7)+(Ni/31)+(Co/23) is 0.10% or less, and O≦0.6%, Al≦4.0%, and (
5/2) High-strength alpha titanium with excellent cold formability, containing O and Al in a range that satisfies O + (1/3) Al≧0.90%, with the remainder substantially consisting of Ti. alloy.
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP26377790A JPH04143236A (en) | 1990-10-03 | 1990-10-03 | High strength alpha type titanium alloy excellent in cold workability |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP26377790A JPH04143236A (en) | 1990-10-03 | 1990-10-03 | High strength alpha type titanium alloy excellent in cold workability |
Publications (1)
Publication Number | Publication Date |
---|---|
JPH04143236A true JPH04143236A (en) | 1992-05-18 |
Family
ID=17394137
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
JP26377790A Pending JPH04143236A (en) | 1990-10-03 | 1990-10-03 | High strength alpha type titanium alloy excellent in cold workability |
Country Status (1)
Country | Link |
---|---|
JP (1) | JPH04143236A (en) |
Cited By (13)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP2012184464A (en) * | 2011-03-04 | 2012-09-27 | Nippon Steel Corp | HIGH-STRENGTH α+β TYPE TITANIUM ALLOY EXCELLENT IN HOT AND COLD WORKABILITY, METHOD FOR PRODUCING THE SAME, AND TITANIUM ALLOY PRODUCT |
US20160201165A1 (en) * | 2015-01-12 | 2016-07-14 | Ati Properties, Inc. | Titanium alloy |
US9869003B2 (en) | 2013-02-26 | 2018-01-16 | Ati Properties Llc | Methods for processing alloys |
US10053758B2 (en) | 2010-01-22 | 2018-08-21 | Ati Properties Llc | Production of high strength titanium |
US10144999B2 (en) | 2010-07-19 | 2018-12-04 | Ati Properties Llc | Processing of alpha/beta titanium alloys |
US10287655B2 (en) | 2011-06-01 | 2019-05-14 | Ati Properties Llc | Nickel-base alloy and articles |
US10337093B2 (en) | 2013-03-11 | 2019-07-02 | Ati Properties Llc | Non-magnetic alloy forgings |
US10370751B2 (en) | 2013-03-15 | 2019-08-06 | Ati Properties Llc | Thermomechanical processing of alpha-beta titanium alloys |
US10422027B2 (en) | 2004-05-21 | 2019-09-24 | Ati Properties Llc | Metastable beta-titanium alloys and methods of processing the same by direct aging |
US10435775B2 (en) | 2010-09-15 | 2019-10-08 | Ati Properties Llc | Processing routes for titanium and titanium alloys |
US10502252B2 (en) | 2015-11-23 | 2019-12-10 | Ati Properties Llc | Processing of alpha-beta titanium alloys |
US10513755B2 (en) | 2010-09-23 | 2019-12-24 | Ati Properties Llc | High strength alpha/beta titanium alloy fasteners and fastener stock |
US11111552B2 (en) | 2013-11-12 | 2021-09-07 | Ati Properties Llc | Methods for processing metal alloys |
-
1990
- 1990-10-03 JP JP26377790A patent/JPH04143236A/en active Pending
Cited By (20)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US10422027B2 (en) | 2004-05-21 | 2019-09-24 | Ati Properties Llc | Metastable beta-titanium alloys and methods of processing the same by direct aging |
US10053758B2 (en) | 2010-01-22 | 2018-08-21 | Ati Properties Llc | Production of high strength titanium |
US10144999B2 (en) | 2010-07-19 | 2018-12-04 | Ati Properties Llc | Processing of alpha/beta titanium alloys |
US10435775B2 (en) | 2010-09-15 | 2019-10-08 | Ati Properties Llc | Processing routes for titanium and titanium alloys |
US10513755B2 (en) | 2010-09-23 | 2019-12-24 | Ati Properties Llc | High strength alpha/beta titanium alloy fasteners and fastener stock |
JP2012184464A (en) * | 2011-03-04 | 2012-09-27 | Nippon Steel Corp | HIGH-STRENGTH α+β TYPE TITANIUM ALLOY EXCELLENT IN HOT AND COLD WORKABILITY, METHOD FOR PRODUCING THE SAME, AND TITANIUM ALLOY PRODUCT |
US10287655B2 (en) | 2011-06-01 | 2019-05-14 | Ati Properties Llc | Nickel-base alloy and articles |
US9869003B2 (en) | 2013-02-26 | 2018-01-16 | Ati Properties Llc | Methods for processing alloys |
US10570469B2 (en) | 2013-02-26 | 2020-02-25 | Ati Properties Llc | Methods for processing alloys |
US10337093B2 (en) | 2013-03-11 | 2019-07-02 | Ati Properties Llc | Non-magnetic alloy forgings |
US10370751B2 (en) | 2013-03-15 | 2019-08-06 | Ati Properties Llc | Thermomechanical processing of alpha-beta titanium alloys |
US11111552B2 (en) | 2013-11-12 | 2021-09-07 | Ati Properties Llc | Methods for processing metal alloys |
US10808298B2 (en) | 2015-01-12 | 2020-10-20 | Ati Properties Llc | Titanium alloy |
RU2703756C2 (en) * | 2015-01-12 | 2019-10-22 | ЭйТиАй ПРОПЕРТИЗ ЭлЭлСи | Titanium alloy |
US10619226B2 (en) | 2015-01-12 | 2020-04-14 | Ati Properties Llc | Titanium alloy |
US10094003B2 (en) * | 2015-01-12 | 2018-10-09 | Ati Properties Llc | Titanium alloy |
US20160201165A1 (en) * | 2015-01-12 | 2016-07-14 | Ati Properties, Inc. | Titanium alloy |
US11319616B2 (en) | 2015-01-12 | 2022-05-03 | Ati Properties Llc | Titanium alloy |
US11851734B2 (en) | 2015-01-12 | 2023-12-26 | Ati Properties Llc | Titanium alloy |
US10502252B2 (en) | 2015-11-23 | 2019-12-10 | Ati Properties Llc | Processing of alpha-beta titanium alloys |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
JP4954369B2 (en) | Method for producing aluminum-magnesium-lithium alloy product | |
JP4486530B2 (en) | Heat-resistant titanium alloy plate excellent in cold workability and method for producing the same | |
JPH04143236A (en) | High strength alpha type titanium alloy excellent in cold workability | |
CA1058425A (en) | Pitting resistant stainless steel alloy having improved hot-working characteristics | |
JP2002155345A (en) | Highly corrosion resistant steel tube having excellent formability and its manufacturing method | |
WO2018198834A1 (en) | Ferritic stainless steel sheet, and production method therefor | |
JP4105962B2 (en) | Sulfuric acid dew-point corrosion steel cold-rolled steel sheet for air preheater heat transfer element and manufacturing method thereof | |
JP7278079B2 (en) | Cold-rolled stainless steel sheet, hot-rolled stainless steel sheet, and method for manufacturing hot-rolled stainless steel sheet | |
JP2001262234A (en) | Method for producing ferritic stainless steel sheet for automotive exhaust system excellent in deep drawability | |
JPS6022061B2 (en) | Manufacturing method of aluminum alloy thin plate for drawer fin | |
JP2019173070A (en) | Al-CONTAINING FERRITIC STAINLESS STEEL MATERIAL EXCELLENT IN FABRICABILITY AND HIGH TEMPERATURE OXIDATION RESISTANCE AND WORKED ARTICLE | |
WO2018198835A1 (en) | Material for cold-rolled stainless steel sheet, and production method therefor | |
JP3260232B2 (en) | Manufacturing method of coastal high weather resistant clad steel sheet | |
JP3352904B2 (en) | Manufacturing method of non-oriented electrical steel sheet | |
JPH06248332A (en) | Production of steel sheet for vessel | |
JPH0839269A (en) | Manufacture of stainless steel and aluminum clad material | |
JPH04143235A (en) | High strength alpha type titanium alloy excellent in formability | |
JPH10204588A (en) | Ferritic stainless steel sheet excellent in workability and roping characteristic, and its manufacture | |
JPH03285017A (en) | Production of resistance welded tube having high vibration damping property | |
JPS5935664A (en) | Production of hot-rolled alpha+beta type titanium alloy sheet having excellent suitability to cold rolling | |
JPH0261033A (en) | Cold rolled steel sheet for deep drawing | |
JPH06184632A (en) | Production of ferritic stainless steel thin sheet | |
JP3232118B2 (en) | Hot-rolled steel strip for construction with excellent fire resistance and toughness and method for producing the same | |
JPS581170B2 (en) | Manufacturing method for hot-rolled steel sheets with excellent enameling properties | |
JPS62270726A (en) | Manufacture of cold rolled steel sheet having superior workability |