JPS6153407B2 - - Google Patents
Info
- Publication number
- JPS6153407B2 JPS6153407B2 JP54010316A JP1031679A JPS6153407B2 JP S6153407 B2 JPS6153407 B2 JP S6153407B2 JP 54010316 A JP54010316 A JP 54010316A JP 1031679 A JP1031679 A JP 1031679A JP S6153407 B2 JPS6153407 B2 JP S6153407B2
- Authority
- JP
- Japan
- Prior art keywords
- rolling
- steel
- final pass
- precipitation
- yield strength
- 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
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- 229910000831 Steel Inorganic materials 0.000 claims description 47
- 239000010959 steel Substances 0.000 claims description 47
- 238000005096 rolling process Methods 0.000 claims description 28
- 230000009467 reduction Effects 0.000 claims description 14
- 229910052720 vanadium Inorganic materials 0.000 claims description 12
- 238000005098 hot rolling Methods 0.000 claims description 7
- 238000000034 method Methods 0.000 claims description 7
- 238000004519 manufacturing process Methods 0.000 claims description 3
- 238000001556 precipitation Methods 0.000 description 16
- 238000005728 strengthening Methods 0.000 description 16
- 238000001816 cooling Methods 0.000 description 8
- 150000001247 metal acetylides Chemical class 0.000 description 8
- 230000000052 comparative effect Effects 0.000 description 6
- 238000012545 processing Methods 0.000 description 5
- 238000005275 alloying Methods 0.000 description 4
- 230000006872 improvement Effects 0.000 description 3
- 239000011150 reinforced concrete Substances 0.000 description 3
- 230000002787 reinforcement Effects 0.000 description 3
- 238000011282 treatment Methods 0.000 description 3
- 239000004567 concrete Substances 0.000 description 2
- 238000010586 diagram Methods 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 238000003754 machining Methods 0.000 description 2
- 238000005259 measurement Methods 0.000 description 2
- 230000035699 permeability Effects 0.000 description 2
- 239000006104 solid solution Substances 0.000 description 2
- 238000005482 strain hardening Methods 0.000 description 2
- 239000000126 substance Substances 0.000 description 2
- 229910018487 Ni—Cr Inorganic materials 0.000 description 1
- 230000032683 aging Effects 0.000 description 1
- 229910001566 austenite Inorganic materials 0.000 description 1
- 238000005452 bending Methods 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 238000007796 conventional method Methods 0.000 description 1
- 230000003247 decreasing effect Effects 0.000 description 1
- 230000006866 deterioration Effects 0.000 description 1
- 230000005674 electromagnetic induction Effects 0.000 description 1
- 238000002474 experimental method Methods 0.000 description 1
- 238000010438 heat treatment Methods 0.000 description 1
- 239000000463 material Substances 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 239000000203 mixture Substances 0.000 description 1
- 229910052758 niobium Inorganic materials 0.000 description 1
- 230000000704 physical effect Effects 0.000 description 1
- 230000001376 precipitating effect Effects 0.000 description 1
- 239000007787 solid Substances 0.000 description 1
- 239000000243 solution Substances 0.000 description 1
- 229910001220 stainless steel Inorganic materials 0.000 description 1
- 239000010935 stainless steel Substances 0.000 description 1
- 230000001629 suppression Effects 0.000 description 1
- 238000012360 testing method Methods 0.000 description 1
- 230000009466 transformation Effects 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
- C21D8/06—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires
- C21D8/065—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires of ferrous alloys
Landscapes
- Engineering & Computer Science (AREA)
- Chemical & Material Sciences (AREA)
- Manufacturing & Machinery (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)
Description
本発明は耐力の高い非磁性棒鋼を製造する方法
に関するものである。
従来から超電導電磁誘導方式リニアモーターカ
ーの基礎コンクリートや磁気測定用建物のコンク
リートなどでは電力ロスや測定誤差発生防止など
の目的から非磁性棒鋼による配筋が要求されてい
る。
非磁性鋼としてはハツドフイールド鋼系の高Ｃ
高Mnのオーステナイト鋼がNi−Cr系ステンレス
鋼に比し経済性の点で優れていることが注目され
ており、非磁性棒鋼として使用され始めている。
高Ｃ高Mnオーステナイト鋼の棒鋼は透磁率1.02
以下という値で非磁性であり、引張強さ、伸び、
及び曲げ性が優れている。
例えば鉄筋コンクリート用棒鋼JIS G3112の熱
間圧延異形棒鋼SD35の規格を満足するものも得
られている。
しかしながら最近更に高い強度を持つ非磁性棒
鋼を要求する声が出ており、従来の高Ｃ高Mnオ
ーステナイト鋼の棒鋼では引張強さの点では大略
満足できるとは言え、耐力の点では満足するだけ
の特性は得られていない。
上記現状に鑑み本発明者等は高Ｃ高Mnオース
テナイト鋼をベースとして多数の実験を行ない高
耐力の非磁性棒鋼を開発することに成功した。
高Ｃ高Mnオーステナイト鋼の強力方法として
は、先ず冷間加工による加工強化を利用する方法
が考えられるが、この方法は経済的に不利であ
り、また冷間加工による組織の変態は磁気特性を
劣化させるという問題点を有している。
次に合金元素添加による固溶強化を利用する方
法があるが、例えばCr、Si、Alなどの添加が試
みられているけれ共、経済的不利を招かない範囲
での合金元素添加量で得られる耐力の向上は10
Kg/mm2程度に過ぎず、大きな耐力向上を望むこと
はできない。
次に挙げられるのは強炭化物形成合金元素を添
加して炭化物の析出によつて強化する方法であ
る。強炭化物形成合金元素としてはNb、Ｖなど
が挙げられるが高Ｃ高Mnオーステナイト鋼の場
合に固溶度の点からＶが最も有利である。Ｖの添
加では70Kg/mm2の耐力が得られるけれ共、この方
法を用いる場合には熱間圧延後に溶体化処理と析
出時効処理といつた後処理が必要であり、製造工
程の複雑化が生じ経済的に不利である。
上記の如く従来の高Ｃ高Mnオーステナイト鋼
棒鋼の強化方法には残されている問題点が存在し
ていることから本発明者等は耐力の向上が大き
く、且つ経済性に富んだ方法を研究した結果、本
発明を完成した。
本発明の構成概略はＶを添加した高Ｃ高Mnオ
ーステナイト鋼の棒鋼熱間圧延時に圧延条件を制
御することによつて熱間圧延における加工歪みの
解放を抑制すると共に圧延後の冷却中にＶ炭化物
を微細に析出させて加工強化と析出強化との二重
の強化によつて耐力の高い非磁性棒鋼を製造する
方法にある。即ちＣ：0.70〜1.20％、Mn：11.0〜
16.0％にＶを添加した高Ｃ高Mnオーステナイト
鋼の棒鋼の熱間圧延時の最終パスの圧下率を10〜
40％とし、且つＶ含有量が0.30％以上0.60％未満
の場合には最終パスの圧延温度を800〜950℃に、
Ｖ含有量が0.60％以上1.00％以下の場合には最終
パスの圧延温度を800〜1050℃にそれぞれ調節し
て圧延し圧延後、大気放冷する。この様にして製
造された棒鋼はＶ炭化物から成る未固溶炭化物の
存在によつて加工歪みの解放が抑制されて加工強
化され、また冷却中に微細析出したＶ炭化物で析
出強化され著しい耐力の向上が得られる。
以下に本発明を構成する各条件について更に詳
細説明する。
Ｃはオーステナイト組織を形成するのに不可欠
な元素であり、通常高Ｃ高Mnオーステナイト鋼
ではＣを0.8〜1.5％が添加されるが、Ｃが高いと
Ｖの固溶量を少なくするし、また粒界炭化物の析
出を促進して靭性を劣化させるから0.70〜1.20％
とした。
Mnもオーステナイト組織の形成に不可欠であ
り、11.0％以上が必要であるが16.0％を超えて添
加しても経済的に不利となるだけであるから11.0
〜16.0％とした。
Ｖの添加量、最終パスの圧下率、最終パスの圧
延温度及び圧延後の冷却速度は熱間加工歪みの解
放を抑制して加工強化を得るのみでなく残存した
加工歪みのため容易ならしめられた微細Ｖ炭化物
の析出によつて析出強化させる点においても重要
である。
第１図、第２図および第３図はそれぞれ0.71％
Ｃ−13.0％Mn；0.71％Ｃ−13.2％Mn−0.40％
Ｖ；および0.72％Ｃ−13.1％Mn−0.80％Ｖ；の成
分から成る鋼片を1150℃で加熱後、800〜1100℃
の所定温度まで放冷し所定温度で圧下率10〜50％
の１パスによる熱間圧延を行ない、その後空冷時
間(a)１秒、(b)10秒、(c)30秒でそれぞれ大気放冷
し、しかる後、水冷して得た鋼材の硬度を測定し
た実験結果を示す図である。尚、図中〇は圧下率
10％、△は圧下率30％、●は圧下率50％の場合を
表わす。Ｖを含まない鋼の場合には第１図に示す
如く加工歪みの解放が急速に起こり、且つ析出強
化が無いため硬度が低い。Ｖを0.40％含んでいる
鋼では第２図に示す如く加工歪みの解放が抑制さ
れ且つ析出強化されて硬度が上昇する傾向がある
が、加工温度が1000℃以上では加工歪みの解放を
抑制しきれず更に歪みが解放されて短時間内での
Ｖ炭化物の析出が微量となり、析出強化もなされ
ていない。Ｖを0.80％含む鋼では第３図に示す如
く加工歪み解放の抑制と析出強化の度合は更に高
まるが、加工温度が1100℃の場合、加工歪み解放
の抑制と析出強化の効果は小さなものとなつてい
る。
之等の知見に基づいて本発明においては最終パ
スの圧延温度の上限を、0.30〜0.60％Ｖの鋼の場
合には950℃；0.60〜1.0％Ｖの鋼の場合には1050
℃としたが、之は加工歪みの解放を抑制し且つ析
出強化が得られることを目的としたからである。
最終パスの圧延温度の下限を800℃としたが、之
は800℃より低い温度では熱間圧延自体が困難と
なるばかりか、温度が低過ぎて冷却中のＶ炭化物
の析出が起き難くなるためである。
最終パスの圧下率は10〜40％としたが、10％未
満では強化に充分な加工歪みを与えることができ
ないし、40％を越える圧下率ではＶを含む高Ｃ高
Mn鋼は変形抵抗が大きいため圧延自体が困難と
なるばかりか、加工率の増大により反えつて加工
歪み解放が促進され、析出強化も少なくなるから
である。圧延後の冷却は大気放冷としたが加工歪
みが残存している場合、Ｖ炭化物の析出は短時間
に起こり大気放冷で充分な析出強化を得ることが
でき、時効処理といつた後処理は必要がなくな
る。
次に本発明の効果を比較例と対比させて実施例
で示す。
本発明実施例と比較例における共試鋼の化学成
分を第１表に示す。
何れも高周波炉で溶製して100Kg鋼塊としたも
のであり、ピレツトに鍛造後、1150℃で加熱し第
２表に示す圧延条件で直径10〜15mmの棒鋼に圧延
した。第３表に本発明の実施例と比較例の機械的
性質と物理的性質を示す。比較例１〜３ではＶを
含まないが、或いは添加量が少ないため耐力が低
い。比較例４、５はＶを0.40％以上含む鋼の場合
であるが最終パスの圧延温度が高いか、或いは最
終パスの圧下率が小さいため充分な加工歪みと炭
化物の析出が得られず耐力の向上は充分でない。
本発明の実施例では耐力が大きく向上し80Kg/
mm2にまで到達する。なお本発明の実施例では耐力
が向上する反面、全伸びが低下し限界曲げ半径が
増大するが、鉄筋コンクリート用棒鋼としては充
分な延性と曲げ性を有している。また本発明の実
施例における透磁率は何れの場合も1.01であり、
従来の高Ｃ高Mnオーステナイト鋼棒鋼の化学成
分と圧延条件を用いた比較例１及び２の場合と差
がなく優れた非磁性鋼であると言うことができ
る。
本発明によつて得られた非磁性棒鋼は耐力が高
いので大きな強化を必要とする鉄筋コンクリート
の配筋などに使用できる。
The present invention relates to a method of manufacturing a non-magnetic steel bar with high yield strength. Conventionally, reinforcement made of non-magnetic steel bars has been required for the foundation concrete of superconducting electromagnetic induction type linear motor cars and the concrete of buildings used for magnetic measurement, in order to prevent power loss and measurement errors. As a non-magnetic steel, there is a high C of hard field steel.
High Mn austenitic steel has attracted attention for its economical advantages over Ni-Cr stainless steel, and has begun to be used as a non-magnetic steel bar.
High C high Mn austenitic steel bar has a magnetic permeability of 1.02
It is non-magnetic with values below, tensile strength, elongation,
and has excellent bendability. For example, we have obtained products that meet the standards for hot rolled deformed steel bars SD35 of JIS G3112 steel bars for reinforced concrete. However, recently there has been a demand for non-magnetic steel bars with even higher strength, and although conventional high-C, high-Mn austenitic steel bars are generally satisfactory in terms of tensile strength, they are only satisfactory in terms of yield strength. characteristics have not been obtained. In view of the above-mentioned current situation, the present inventors conducted numerous experiments based on high C, high Mn austenitic steel and succeeded in developing a high yield strength non-magnetic steel bar. The first possible way to strengthen high C, high Mn austenitic steel is to use cold working to strengthen it, but this method is economically disadvantageous, and the transformation of the structure due to cold working impairs the magnetic properties. It has the problem of deterioration. Next, there is a method that utilizes solid solution strengthening by adding alloying elements. For example, addition of Cr, Si, Al, etc. has been attempted, but it can be obtained by adding alloying elements in amounts that do not cause economic disadvantage. Increased strength by 10
It is only about Kg/mm 2 , and we cannot expect a significant improvement in yield strength. The next method is to add a strong carbide-forming alloying element to strengthen the steel by precipitation of carbides. Examples of strong carbide-forming alloying elements include Nb and V, but in the case of high C, high Mn austenitic steel, V is most advantageous from the viewpoint of solid solubility. By adding V, a yield strength of 70 kg/mm 2 can be obtained, but when using this method, post-treatments such as solution treatment and precipitation aging treatment are required after hot rolling, which complicates the manufacturing process. This is economically disadvantageous. As mentioned above, there are still problems with the conventional method of strengthening high C, high Mn austenitic steel bars, so the present inventors have researched a method that can greatly improve yield strength and is highly economical. As a result, the present invention was completed. The outline of the structure of the present invention is to control the rolling conditions during hot rolling of a high C, high Mn austenitic steel bar added with V, thereby suppressing the release of working strain during hot rolling, and suppressing the release of working strain during cooling after rolling. The method consists in producing a non-magnetic steel bar with high yield strength through double strengthening of work strengthening and precipitation strengthening by finely precipitating carbides. That is, C: 0.70~1.20%, Mn: 11.0~
The reduction ratio of the final pass during hot rolling of a high C high Mn austenitic steel bar with 16.0% V added is 10~
40%, and when the V content is 0.30% or more and less than 0.60%, the final pass rolling temperature is 800 to 950°C,
When the V content is 0.60% or more and 1.00% or less, the final pass rolling temperature is adjusted to 800 to 1050°C, and after rolling, the product is allowed to cool in the atmosphere. The steel bars produced in this way are work-strengthened by suppressing the release of working strain due to the presence of undissolved carbides consisting of V carbides, and are precipitation-strengthened by the finely precipitated V carbides during cooling, resulting in significant yield strength. Improvement can be obtained. Each condition constituting the present invention will be explained in more detail below. C is an essential element for forming an austenitic structure, and usually 0.8 to 1.5% of C is added to high C, high Mn austenitic steel, but high C reduces the amount of solid solution of V, and also 0.70 to 1.20% because it promotes the precipitation of grain boundary carbides and deteriorates toughness.
And so. Mn is also essential for the formation of the austenite structure, and it is necessary to add more than 11.0%, but adding more than 16.0% will only be economically disadvantageous.
~16.0%. The amount of V added, the rolling reduction rate in the final pass, the rolling temperature in the final pass, and the cooling rate after rolling are adjusted not only to suppress the release of hot working strain and obtain work strengthening, but also to ease the residual working strain. It is also important in terms of precipitation strengthening due to the precipitation of fine V carbides. Figures 1, 2 and 3 are each 0.71%
C-13.0%Mn; 0.71%C-13.2%Mn-0.40%
and 0.72%C-13.1%Mn-0.80%V; after heating it at 1150℃, it was heated to 800-1100℃.
Allow to cool to a specified temperature and reduce the reduction rate to 10 to 50% at the specified temperature.
After hot rolling with one pass, the steel was cooled in the atmosphere for (a) 1 second, (b) 10 seconds, and (c) 30 seconds, and then water-cooled and the hardness of the obtained steel material was measured. FIG. 2 is a diagram showing the experimental results. In addition, 〇 in the figure is the rolling reduction rate.
10%, △ indicates a rolling reduction of 30%, ● indicates a rolling reduction of 50%. In the case of steel that does not contain V, the release of working strain occurs rapidly as shown in FIG. 1, and there is no precipitation strengthening, so the hardness is low. As shown in Figure 2, steel containing 0.40% V tends to suppress the release of working strain and undergo precipitation strengthening, resulting in an increase in hardness. In addition, the strain was released, and a very small amount of V carbide precipitated within a short period of time, and no precipitation strengthening occurred. In steel containing 0.80% V, the degree of suppression of processing strain release and precipitation strengthening is further increased as shown in Figure 3, but when the processing temperature is 1100°C, the effects of suppressing processing strain release and precipitation strengthening are small. It's summery. Based on these findings, in the present invention, the upper limit of the rolling temperature in the final pass is set to 950°C in the case of 0.30 to 0.60% V steel; 1050°C in the case of 0.60 to 1.0% V steel.
℃ because the purpose was to suppress the release of processing strain and obtain precipitation strengthening.
The lower limit of the rolling temperature for the final pass was set at 800°C, because not only would hot rolling itself be difficult at a temperature lower than 800°C, but the temperature would be too low, making it difficult for V carbide to precipitate during cooling. It is. The rolling reduction ratio in the final pass was set at 10 to 40%, but if it is less than 10%, it will not be possible to give sufficient machining strain for strengthening, and if the rolling reduction ratio exceeds 40%, it will result in high C, including V.
This is because not only is Mn steel difficult to roll due to its large deformation resistance, but also an increase in the working rate promotes release of working strain and reduces precipitation strengthening. Cooling after rolling was performed by air cooling, but if machining distortion remains, precipitation of V carbides occurs in a short period of time, and sufficient precipitation strengthening can be obtained by air cooling. is no longer needed. Next, the effects of the present invention will be shown in Examples in comparison with comparative examples. Table 1 shows the chemical components of the joint test steels in the examples of the present invention and comparative examples. All of the steel ingots were made into 100 kg steel ingots by melting in a high frequency furnace, and after being forged into pillars, they were heated at 1150°C and rolled into steel bars with a diameter of 10 to 15 mm under the rolling conditions shown in Table 2. Table 3 shows the mechanical properties and physical properties of Examples of the present invention and Comparative Examples. Comparative Examples 1 to 3 do not contain V, or the amount added is small, so the yield strength is low. Comparative Examples 4 and 5 involve steel containing 0.40% or more of V, but because the rolling temperature in the final pass is high or the rolling reduction rate in the final pass is small, sufficient processing strain and carbide precipitation cannot be obtained, resulting in a decrease in yield strength. Improvement is not enough. In the example of the present invention, the yield strength is greatly improved to 80Kg/
reaching up to mm 2 . In the examples of the present invention, although the yield strength is improved, the total elongation is decreased and the limit bending radius is increased, but the steel bars have sufficient ductility and bendability as steel bars for reinforced concrete. In addition, the magnetic permeability in the examples of the present invention is 1.01 in all cases,
It can be said that this is an excellent non-magnetic steel with no difference from Comparative Examples 1 and 2, which used the chemical composition and rolling conditions of conventional high C, high Mn austenitic steel bars. Since the non-magnetic steel bar obtained by the present invention has a high yield strength, it can be used for reinforcement of reinforced concrete that requires large reinforcement.
【表】【table】
【表】【table】
【表】【table】
図はＶ含有量を変えた３種の鋼について圧延温
度、圧下率、圧延後の空冷時間をそれぞれ(a)１
秒、(b)10秒、(c)30秒に変化させて圧延した場合の
硬度の変化を示す図であり、第１図は0.71％Ｃ−
13.0％Mn鋼；第２図は0.71％Ｃ−13.2％Mn−
0.40％Ｖ鋼；第３図は0.72％Ｃ−13.1％Mn−0.80
％Ｖ鋼の場合を示す。
〇……圧下率10％の場合、△……圧下率30％の
場合、●……圧下率50％の場合。
The figure shows rolling temperature, reduction ratio, and air cooling time after rolling for three types of steel with different V contents (a) 1
Fig. 1 is a diagram showing changes in hardness when rolling is performed for 10 seconds, (b) 10 seconds, and (c) 30 seconds.
13.0%Mn steel; Figure 2 shows 0.71%C-13.2%Mn-
0.40%V steel; Figure 3 shows 0.72%C-13.1%Mn-0.80
%V steel is shown. 〇...When the rolling reduction rate is 10%, △...When the rolling reduction rate is 30%,●...When the rolling reduction rate is 50%.
Claims (1)
0.30〜1.00％を添加した高Ｃ高Mnオーステナイ
ト鋼棒鋼の熱間圧延時の最終パス圧下率を10〜40
％とし且つＶ含有量に対応して最終パスの圧延温
度をＶ含有量が0.30％以上0.60％未満の場合は
800〜950℃の範囲で、Ｖ含有量が0.60％以上1.00
％以下の場合は800〜1050℃の範囲に設定して圧
延後、大気放冷することを特徴とする高耐力非磁
性棒鋼製造方法。1 C: 0.70-1.20%, Mn: 11.0-16.0%, V:
The final pass reduction rate during hot rolling of high C high Mn austenitic steel bar with addition of 0.30 to 1.00% is 10 to 40.
%, and the final pass rolling temperature is set according to the V content when the V content is 0.30% or more and less than 0.60%.
In the range of 800 to 950℃, V content is 0.60% or more 1.00
% or less, the method for manufacturing a high strength non-magnetic steel bar is characterized in that the temperature is set in the range of 800 to 1050°C, and after rolling, the steel bar is allowed to cool in the atmosphere.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP1031679A JPS55104428A (en) | 1979-02-02 | 1979-02-02 | Production of high yield sprength non-magnetic bar steel |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP1031679A JPS55104428A (en) | 1979-02-02 | 1979-02-02 | Production of high yield sprength non-magnetic bar steel |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS55104428A JPS55104428A (en) | 1980-08-09 |
| JPS6153407B2 true JPS6153407B2 (en) | 1986-11-18 |
Family
ID=11746828
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP1031679A Granted JPS55104428A (en) | 1979-02-02 | 1979-02-02 | Production of high yield sprength non-magnetic bar steel |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS55104428A (en) |
Families Citing this family (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP5842732B2 (en) * | 2012-05-18 | 2016-01-13 | 新日鐵住金株式会社 | Billet manufacturing method |
| BR112017005540A2 (en) | 2014-10-01 | 2017-12-05 | Nippon Steel & Sumitomo Metal Corp | ? high strength steel material for oil well and oil industry tubular goods? |
| JP7135737B2 (en) * | 2018-10-31 | 2022-09-13 | 日本製鉄株式会社 | Austenitic hot-rolled steel sheet, manufacturing method thereof, and wear-resistant parts |
Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5118917A (en) * | 1974-08-09 | 1976-02-14 | Nippon Steel Corp | Jinseinosugureta kokyodooosutenaitokono seizoho |
| JPS52150720A (en) * | 1976-06-10 | 1977-12-14 | Sumitomo Metal Ind Ltd | Nonmagnetic steel material superior in mechanical properties |
| JPS52150721A (en) * | 1976-06-10 | 1977-12-14 | Sumitomo Metal Ind Ltd | Nonmagnetic reinforcing iron |
| JPS579610A (en) * | 1980-06-16 | 1982-01-19 | Shin Meiwa Ind Co Ltd | Powder conveyor |
-
1979
- 1979-02-02 JP JP1031679A patent/JPS55104428A/en active Granted
Patent Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5118917A (en) * | 1974-08-09 | 1976-02-14 | Nippon Steel Corp | Jinseinosugureta kokyodooosutenaitokono seizoho |
| JPS52150720A (en) * | 1976-06-10 | 1977-12-14 | Sumitomo Metal Ind Ltd | Nonmagnetic steel material superior in mechanical properties |
| JPS52150721A (en) * | 1976-06-10 | 1977-12-14 | Sumitomo Metal Ind Ltd | Nonmagnetic reinforcing iron |
| JPS579610A (en) * | 1980-06-16 | 1982-01-19 | Shin Meiwa Ind Co Ltd | Powder conveyor |
Also Published As
| Publication number | Publication date |
|---|---|
| JPS55104428A (en) | 1980-08-09 |
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