JPH07109012B2 - Manufacturing method of super workable cold rolled steel sheet - Google Patents
Manufacturing method of super workable cold rolled steel sheetInfo
- Publication number
- JPH07109012B2 JPH07109012B2 JP63330201A JP33020188A JPH07109012B2 JP H07109012 B2 JPH07109012 B2 JP H07109012B2 JP 63330201 A JP63330201 A JP 63330201A JP 33020188 A JP33020188 A JP 33020188A JP H07109012 B2 JPH07109012 B2 JP H07109012B2
- Authority
- JP
- Japan
- Prior art keywords
- rolling
- product
- value
- steel sheet
- temperature
- 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.)
- Expired - Fee Related
Links
- 238000004519 manufacturing process Methods 0.000 title claims description 9
- 239000010960 cold rolled steel Substances 0.000 title claims description 8
- 239000000463 material Substances 0.000 claims description 22
- 238000005096 rolling process Methods 0.000 claims description 22
- 229910000831 Steel Inorganic materials 0.000 claims description 17
- 239000010959 steel Substances 0.000 claims description 17
- 230000009466 transformation Effects 0.000 claims description 12
- 238000005097 cold rolling Methods 0.000 claims description 10
- 229910052758 niobium Inorganic materials 0.000 claims description 10
- 229910052719 titanium Inorganic materials 0.000 claims description 8
- 229910052757 nitrogen Inorganic materials 0.000 claims description 6
- 238000001953 recrystallisation Methods 0.000 claims description 5
- 238000000034 method Methods 0.000 claims description 4
- 238000004804 winding Methods 0.000 claims description 4
- 229910052742 iron Inorganic materials 0.000 claims description 3
- 238000005554 pickling Methods 0.000 claims description 3
- 239000012535 impurity Substances 0.000 claims description 2
- 230000001050 lubricating effect Effects 0.000 claims 1
- 239000000047 product Substances 0.000 description 25
- 238000010438 heat treatment Methods 0.000 description 13
- 238000005098 hot rolling Methods 0.000 description 5
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 3
- 229910000655 Killed steel Inorganic materials 0.000 description 3
- 229910052799 carbon Inorganic materials 0.000 description 3
- 239000000203 mixture Substances 0.000 description 3
- 239000002244 precipitate Substances 0.000 description 3
- 239000000126 substance Substances 0.000 description 3
- 230000015572 biosynthetic process Effects 0.000 description 2
- 238000005265 energy consumption Methods 0.000 description 2
- 238000005461 lubrication Methods 0.000 description 2
- 239000006104 solid solution Substances 0.000 description 2
- 229910001209 Low-carbon steel Inorganic materials 0.000 description 1
- 239000010953 base metal Substances 0.000 description 1
- 230000000052 comparative effect Effects 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- 230000001771 impaired effect Effects 0.000 description 1
- 230000010354 integration Effects 0.000 description 1
- 229910052698 phosphorus Inorganic materials 0.000 description 1
- 238000000746 purification Methods 0.000 description 1
- 239000002994 raw material Substances 0.000 description 1
- 239000002344 surface layer Substances 0.000 description 1
- 229910052715 tantalum Inorganic materials 0.000 description 1
- 229910052726 zirconium Inorganic materials 0.000 description 1
- 229910000859 α-Fe Inorganic materials 0.000 description 1
Classifications
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B3/00—Rolling materials of special alloys so far as the composition of the alloy requires or permits special rolling methods or sequences ; Rolling of aluminium, copper, zinc or other non-ferrous metals
- B21B3/02—Rolling special iron alloys, e.g. stainless steel
Landscapes
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Metal Rolling (AREA)
- Heat Treatment Of Steel (AREA)
- Heat Treatment Of Sheet Steel (AREA)
Description
【発明の詳細な説明】 （産業上の利用分野） 本発明は、深絞り性に優れた超加工性冷延鋼板の製造方
法に関するものである。TECHNICAL FIELD The present invention relates to a method for producing a super-workable cold-rolled steel sheet having excellent deep drawability.
（従来の技術） 鋼中の固溶しているＣおよびＮを、Ti,Nb,Ta,Zrといっ
た炭窒化物形成元素を鋼に添加することによって析出物
として析出させて母材を高純化し、これによって優れた
深絞り性を有する冷延鋼板を得る技術がよく知られてい
る。特に、極低炭素鋼にTiを添加したTi−キルド鋼
（「鉄と鋼」第61巻（1975）第817頁）,TiとNbを複合添
加したTi−Nbキルド鋼およびNbとＢを複合添加したNb−
Ｂキルド鋼等が既に生産され、ｒ値が2.0前後の高い値
をもつ深絞り用冷延鋼板として販売されている。(Prior Art) C and N in solid solution in steel are precipitated as precipitates by adding carbonitride forming elements such as Ti, Nb, Ta and Zr to the steel to make the base metal highly purified. A technique for obtaining a cold-rolled steel sheet having excellent deep drawability by this is well known. In particular, Ti-killed steel in which Ti is added to ultra-low carbon steel ("Iron and Steel," Vol. 61 (1975) p. 817), Ti-Nb killed steel in which Ti and Nb are added in combination, and Nb and B in combination are added. Nb added
B-killed steel and other products have already been produced and are sold as deep-drawn cold-rolled steel sheets with a high r value of around 2.0.
これらの冷延鋼板の製造プロセスは、1200℃前後に鋼を
加熱し、仕上温度がAr3変態点以上となる条件下に熱間
圧延して巻き取り、酸洗工程を経て90％前後の圧延率と
なる高圧下冷間圧延を行い、次いで再結晶処理して製品
とするプロセスである。The manufacturing process of these cold-rolled steel sheets is to heat the steel to around 1200 ° C, hot-roll it under conditions where the finishing temperature is at or above the Ar 3 transformation point, wind it, and pass it through a pickling process to roll it to around 90%. In this process, cold rolling is performed under high pressure at a certain rate, and then recrystallization is performed to obtain a product.
しかしながら、この先行技術によるときは、省エネルギ
という観点からは次のような問題がある。即ち、高いｒ
値を有する製品を得るために、圧延仕上温度をAr3変態
点以上としている処から、素材の加熱エネルギ消費量を
少なくする低温加熱を行えない。However, this prior art has the following problems from the viewpoint of energy saving. That is, high r
In order to obtain a product having a value, since the rolling finishing temperature is set to the Ar 3 transformation point or higher, low temperature heating that reduces the consumption of heating energy of the raw material cannot be performed.
また、低温加熱が可能であれば、素材加熱段階で生成す
る炭窒化物は高温加熱材に比しその大きさが大きくまた
量も多く、従って母材の高純化が進み、製品のｒ値を高
くする点からも有利である。しかしながら、従来技術に
おいて、素材を低温加熱しAr3変態点以下の温度域で圧
延すると、材料表面層において深絞り性を良好ならしめ
るに有利な方位である（111）の集積度の高い集合組織
の形成が抑制され、製品のｒ値が低下する。Also, if low temperature heating is possible, the carbonitrides generated in the material heating stage are large and large in amount as compared with the high temperature heating material, so that the base material is highly purified and the r value of the product is increased. It is also advantageous from the viewpoint of increasing the height. However, in the prior art, when the material is heated at a low temperature and rolled in the temperature range below the Ar 3 transformation point, the texture with a high degree of integration of (111) is an orientation that is advantageous for achieving good deep drawability in the material surface layer. Formation is suppressed and the r value of the product is reduced.
（発明が解決しようとする課題） 本発明は、前記従来技術における問題点即ち、圧延仕上
温度をAr3変態点以上としなければ高いｒ値を有する製
品が得られず、従って素材を低温加熱することが不可能
であるという問題を解決し、製品特性ならびに省エネル
ギ双方の観点から優れた製造プロセスを提供することを
目的としてなされた。(Problems to be Solved by the Invention) The present invention has a problem in the above-mentioned prior art, that is, a product having a high r value cannot be obtained unless the rolling finishing temperature is not lower than the Ar 3 transformation point, and therefore the material is heated at a low temperature. It was made for the purpose of solving the problem that it is impossible and providing an excellent manufacturing process from the viewpoint of both product characteristics and energy saving.
（課題を解決するための手段） 本発明の要旨とする処は、重量で、Ｃ≦0.01％,N≦0.01
％，さらにTiおよびNbの何れか一方または双方をC/12＋
N/14＜1.2（Ti/48＋Nb/93）なる関係を満足する如く含
有し、残部Feおよび不可避的不純物からなる鋼を、Ar3
変態点以下、800℃以上の温度域に加熱し、730℃以上、
Ar3変態点以下の温度域で圧延ロールと材料間の摩擦係
数が0.2以下となる如く潤滑を施しつつ合計圧下率が90
％超となる圧延を行い、650℃以上の温度域で巻き取
り、然る後通常の酸洗を行い次いで圧下率75％以上の冷
間圧延を行った後、再結晶処理を施すことを特徴とする
超加工性冷延鋼板の製造方法にある。(Means for Solving the Problem) The gist of the present invention is, by weight, C ≦ 0.01%, N ≦ 0.01.
%, And either or both Ti and Nb are C / 12 +
N / 14 <1.2 (Ti / 48 + Nb / 93) the relationship was as containing satisfying, steel balance consisting of Fe and unavoidable impurities, Ar 3
Below the transformation point, heat to a temperature range of 800 ℃ or more, 730 ℃ or more,
In the temperature range below the Ar 3 transformation point, the total rolling reduction was 90
% Rolling, winding in a temperature range of 650 ° C or higher, then normal pickling, cold rolling with a rolling reduction of 75% or higher, and then recrystallization treatment And a method of manufacturing a super-workable cold-rolled steel sheet.
以下に、本発明を詳細に説明する。The present invention will be described in detail below.
本発明において、TiおよびNbの何れか一方または双方を
重量で、 C/12＋N/14＜1.2（Ti/48＋Nb/93）なる関係を満足する
如く鋼中に添加するようにしたのは、この条件を満足せ
しめることにより、鋼中に固溶しているＣおよびＮを析
出物の形で固定でき、製品の深絞り性を良好ならしめる
に有利な方位である（111）＜112＞、（554）＜225＞等
の集積度の高い集合組織を有する鋼板を得ることができ
るからである。In the present invention, one or both of Ti and Nb, by weight, is added to the steel so as to satisfy the relationship of C / 12 + N / 14 <1.2 (Ti / 48 + Nb / 93). By satisfying the above condition, C and N which are solid-solved in the steel can be fixed in the form of precipitates, which is an advantageous azimuth for improving the deep drawability of the product (111) <112>, (554). ) It is possible to obtain a steel sheet having a highly integrated texture such as <225>.
一方、Ｃ≦0.01％、Ｎ≦0.01％としたのは、これらの量
を超えてＣ、Ｎが鋼中に存在すると、製品の加工性を損
なうのみならず上記条件式を満足せしめるに必要なTi或
はNbの量が多くなり、製造コストの面で不利となるから
である。また、Ti、Nbを多量に鋼に添加すると、これら
元素の固溶硬化によって製品の強度が上昇し、加工性の
低下を招くとともに、再結晶温度が高くなり熱処理にお
けるエネルギ消費量を多大なものとする等の問題を生じ
るから、Ti≦0.3％、Nb≦0.2％とするのが好ましい。On the other hand, C ≦ 0.01% and N ≦ 0.01% are necessary because if C and N are present in the steel in excess of these amounts, not only the workability of the product is impaired but also the above conditional expression is satisfied. This is because the amount of Ti or Nb increases, which is disadvantageous in terms of manufacturing cost. In addition, when Ti and Nb are added to steel in a large amount, the solid solution hardening of these elements increases the strength of the product, lowers the workability, and raises the recrystallization temperature, resulting in a large energy consumption in heat treatment. Therefore, it is preferable that Ti ≦ 0.3% and Nb ≦ 0.2%.
なお、本発明において、鋼の他の成分としては、深絞り
用冷延鋼板として通常含まれる成分即ち、Mn≦0.30％、
Si≦0.2％、Ｐ≦0.03％、Ｓ≦0.02％、Al≦0.08％を含
有せしめてもよい。また、0.0050％以下のＢを添加して
も本発明の趣旨を損なうものではない。In the present invention, as other components of the steel, the components that are usually included as deep-drawn cold-rolled steel sheet, that is, Mn ≦ 0.30%,
You may contain Si <= 0.2%, P <= 0.03%, S <= 0.02%, Al <= 0.08%. Further, addition of 0.0050% or less of B does not impair the gist of the present invention.
次に、製造プロセスについて説明する。Next, the manufacturing process will be described.
素材の加熱温度をAr3変態点以下としたのは、Ti,Nb等の
炭窒化物形成元素の溶解度がγ域に比しα域の方がはる
かに小さく炭窒化物の生成が容易に起こり、母材の高純
化が進むからである。また、素材の加熱温度の下限を80
0℃としたのは、この温度に満たない低い温度に加熱す
ると、730℃以上の温度域で熱間圧延を終了させること
が困難となるからである。The heating temperature of the material was set to the Ar 3 transformation point or lower because the solubility of carbonitride forming elements such as Ti and Nb is much smaller in the α region than in the γ region and carbonitride formation easily occurs. , Because the purification of the base material is advanced. In addition, the lower limit of the heating temperature of the material is 80
The reason why the temperature is 0 ° C. is that it becomes difficult to finish the hot rolling in a temperature range of 730 ° C. or higher when heating to a temperature lower than this temperature.
730℃以上の温度域で熱間圧延を終了させるように規定
したのは、この温度以上の領域で仕上圧延を完了させ、
650℃以上の温度域で巻き取るようにすることにより、
熱延板の大部分が再結晶組織となり、製品のｒ値を高く
することができるからである。It was stipulated that the hot rolling should be terminated in the temperature range of 730 ° C or higher because the finish rolling was completed in the temperature range of this temperature or higher,
By winding in a temperature range of 650 ° C or higher,
This is because most of the hot-rolled sheet has a recrystallized structure and the r value of the product can be increased.
熱延板に未再結晶組織が多く残ると、ND＜111＞方位
が発達せず、高いｒ値を有する製品が得られない。If a large amount of unrecrystallized structure remains in the hot-rolled sheet, the ND <111> orientation will not develop and a product having a high r value cannot be obtained.
圧延ロールと材料間の摩擦係数が0.2以下となる如く潤
滑を施しながら圧延するのは、かくすることにより鋼板
表面にND＜111＞方位を有する集合組織を発達させ、
製品のｒ値を高くすることができるからである。Rolling with lubrication so that the friction coefficient between the rolling roll and the material is 0.2 or less is done by developing a texture with ND <111> orientation on the surface of the steel sheet,
This is because the r value of the product can be increased.
熱間圧延における合計圧下率を90％超としたのは、これ
以下の圧下率では熱延板の粒径が粗大であり再結晶が十
分に起きないことに起因して製品のｒ値が低くなりかつ
リジングが発生するからである。The total rolling reduction in hot rolling was set to more than 90% because the grain size of the hot-rolled sheet was coarse and recrystallization did not occur sufficiently at a rolling reduction below this value, and the r value of the product was low. This is because ridging occurs.
次に、冷間圧延における圧下率を規定した理由を説明す
る。Next, the reason for defining the rolling reduction in cold rolling will be described.
発明者等は、冷延率と製品におけるｒ値の関係について
調査した結果、Ar3変態点以下の温度域で熱間圧延され
た材料は、Ar3変態点を超える温度域で熱間圧延を仕上
げられた材料とは異なり、75％以上の圧下率を適用する
冷間圧延を施すことにより、製品のｒ値を高くすること
ができかつ、異方性の指標である｜△r|を小さくするこ
とができることを見出した。そこで、本発明においては
第１図に示すように、｜△r|を0.6以下とすべく、冷延
率を75％以上とするようにした。As a result of investigating the relationship between the cold rolling rate and the r value in the product, the inventors have found that a material hot-rolled in a temperature range below the Ar 3 transformation point is hot-rolled in a temperature range above the Ar 3 transformation point. Unlike finished materials, cold rolling that applies a reduction of 75% or more can increase the r-value of the product and reduces | Δr |, which is an anisotropy index. I found that I can do it. Therefore, in the present invention, as shown in FIG. 1, the cold rolling rate is set to 75% or more so that | Δr | is set to 0.6 or less.
（実施例） 本発明の実施例を、比較例とともに説明する。(Example) The Example of this invention is demonstrated with a comparative example.
表１に示す成分組成を有する鋼を、種々の条件で熱間圧
延および冷間圧延した。Steels having the chemical compositions shown in Table 1 were hot-rolled and cold-rolled under various conditions.
これらの圧延条件と製品特性を、表２に示す。冷延板に
は、800℃×２分間の連続焼鈍を施した。Table 2 shows these rolling conditions and product characteristics. The cold rolled sheet was continuously annealed at 800 ° C. for 2 minutes.
材料ＡおよびＢは、C/12＋N/14＜1.2（Ti/48＋Nb/93）
の条件を満足しておらず、圧延条件が本発明に規定する
条件を満足しているにも拘わらず、製品のｒ値が低く良
好な深絞り性を期待できない。Materials A and B are C / 12 + N / 14 <1.2 (Ti / 48 + Nb / 93)
Although the rolling condition satisfies the conditions defined in the present invention, the r value of the product is low and good deep drawability cannot be expected.
これに比し、本発明で規定する化学成分条件を満足する
材料Ｃ、Ｄ、Ｅに、本発明に規定する条件を満足する圧
延を施して得られた製品は、高い値と低い｜△r|値な
らびに高い延性Elを示した。かかる製品は、超加工性鋼
板としての使用が可能となる。On the contrary, the products obtained by rolling the materials C, D and E satisfying the chemical composition conditions specified in the present invention to satisfy the conditions specified in the present invention have high values and low | Δr | Value and high ductility El. Such a product can be used as a super workable steel plate.
これに比し、本発明で規定する化学成分条件を満足する
材料Ｃ、Ｄ、Ｅであっても、素材加熱温度が1130℃と本
発明に規定する温度を超えるNo.8は、炭窒化物が微細に
析出し、延性が劣る。また、熱間圧延仕上温度或いは巻
き取り温度が低く、熱延板が十分再結晶しなかったNo.5
および６は、製品の値が低く｜△r|値が高く、成形性
が劣る。On the other hand, even if the materials C, D, and E satisfy the chemical composition conditions specified in the present invention, No. 8 whose material heating temperature exceeds 1130 ° C and the temperature specified in the present invention is carbonitride. Is finely precipitated and the ductility is poor. In addition, the hot rolling finishing temperature or winding temperature was low, and the hot rolled sheet did not recrystallize sufficiently.
In Nos. 6 and 6, the product value is low and the | Δr | value is high, and the moldability is poor.
一方、Ar3変態点以下、730℃以上の温度域での圧延にお
ける合計圧下率が90％以下のNo.は、製品の値は低
い。これは、熱延板のフェライト粒径が大きかったこと
に起因していると思われる。冷延率の低いNo.9は、第１
図に示す処と同様に、値が低く｜△r|が大きい。On the other hand, No. having a total rolling reduction of 90% or less in the temperature range of Ar 3 transformation point or lower and 730 ° C. or higher has a low product value. This is probably because the ferrite grain size of the hot rolled sheet was large. No. 9 with low cold rolling rate is No. 1
As in the case shown in the figure, the value is low and | Δr | is large.
また、熱間圧延において、圧延ロールと材料間に潤滑を
施し両者間の摩擦係数を0.2以下に維持して圧延してい
るので、無潤滑で熱間圧延したものに比し、深絞り性に
優れていることが分かる。Also, in hot rolling, lubrication is applied between the rolling roll and the material, and the friction coefficient between the two is maintained at 0.2 or less. It turns out to be excellent.
（発明の効果） 本発明によれば、素材加熱温度を低くすることができる
から、加熱のためのエネルギ消費量を大幅に低減でき
る。また、材質面においても、素材の低温加熱は析出物
を粗大化させるから、製品の延性およびｒ値を向上させ
るのに有利である。 (Effect of the Invention) According to the present invention, since the material heating temperature can be lowered, the energy consumption for heating can be significantly reduced. Also in terms of material, heating the material at low temperature coarsens the precipitates, which is advantageous for improving the ductility and r-value of the product.
一方、本発明に規定する冷延率を採ることにより、製品
における異方性の問題も解決され、高延性、高値そし
て低い異方性をもつ超加工性鋼板を製造できる。On the other hand, by adopting the cold rolling rate specified in the present invention, the problem of anisotropy in the product is solved, and a super-workable steel sheet having high ductility, high value and low anisotropy can be manufactured.
叙上のように、本発明は、超加工性鋼板を得るに際し、
製造コストを低減させるとともに材質の向上を可能にす
る、工業的に価値の高い発明である。As described above, the present invention provides a super workable steel sheet,
It is an industrially valuable invention that enables reduction of manufacturing cost and improvement of material quality.
第１図は製品のｒ値と冷延率の関係を示す図である。 図中のL,D,Cはそれぞれ圧延方向に平行,45゜，垂直方向
のｒ値を示す。また,|△r|は、＝（rL＋2rD＋rC）/
4,|△r|＝|rL＋rC−2rD|/2より求めた値である。FIG. 1 is a diagram showing the relationship between the r value of a product and the cold rolling rate. L, D, and C in the figure indicate r-values parallel to the rolling direction, 45 °, and vertical, respectively. Also, | △ r | is = (r L ＋ 2r D ＋ r C ) /
It is a value obtained from 4, | Δr | = | r L + r C −2r D | / 2.
Claims (1)
TiおよびNbの何れか一方または双方をC/12＋N/14＜1.2
（Ti/48＋Nb/93）なる関係を満足する如く含有し、残部
Feおよび不可避的不純物からなる鋼を、Ar3変態点以
下、800℃以上の温度域に加熱し、730℃以上、Ar3変態
点以下の温度域で圧延ロールと材料間の摩擦係数が0.2
以下となる如く潤滑を施しつつ合計圧下率が90％超とな
る圧延を行い、650℃以上の温度域で巻き取り、然る後
通常の酸洗を行い、次いで圧下率75％以上の冷間圧延を
行った後、再結晶処理を施すことを特徴とする超加工性
冷延鋼板の製造方法。1. By weight, C ≦ 0.01%, N ≦ 0.01%, and
Either or both of Ti and Nb are C / 12 + N / 14 <1.2
Contains so as to satisfy the relationship of (Ti / 48 + Nb / 93), the balance
Steel consisting of Fe and unavoidable impurities is heated to a temperature range of Ar 3 transformation point or lower and 800 ° C or higher, and a friction coefficient between the rolling roll and the material is 0.2 in a temperature range of 730 ° C or higher and Ar 3 transformation point or lower.
Rolling is performed with the total rolling reduction exceeding 90% while lubricating as shown below, winding in a temperature range of 650 ° C or higher, then normal pickling, and then cold rolling with a rolling reduction of 75% or higher. A method for manufacturing a super-workable cold-rolled steel sheet, which comprises performing recrystallization treatment after rolling.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP63330201A JPH07109012B2 (en) | 1988-12-27 | 1988-12-27 | Manufacturing method of super workable cold rolled steel sheet |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP63330201A JPH07109012B2 (en) | 1988-12-27 | 1988-12-27 | Manufacturing method of super workable cold rolled steel sheet |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH02175822A JPH02175822A (en) | 1990-07-09 |
| JPH07109012B2 true JPH07109012B2 (en) | 1995-11-22 |
Family
ID=18229967
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP63330201A Expired - Fee Related JPH07109012B2 (en) | 1988-12-27 | 1988-12-27 | Manufacturing method of super workable cold rolled steel sheet |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH07109012B2 (en) |
Family Cites Families (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH062990B2 (en) * | 1983-08-22 | 1994-01-12 | 東洋インキ製造株式会社 | Liquid colorant for polyester fiber |
| JPH07812B2 (en) * | 1984-11-16 | 1995-01-11 | 新日本製鐵株式会社 | Manufacturing method of cold-rolled steel sheet for deep drawing |
-
1988
- 1988-12-27 JP JP63330201A patent/JPH07109012B2/en not_active Expired - Fee Related
Also Published As
| Publication number | Publication date |
|---|---|
| JPH02175822A (en) | 1990-07-09 |
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