JPH03287726A - Production of boron steel sheet - Google Patents
Production of boron steel sheetInfo
- Publication number
- JPH03287726A JPH03287726A JP9076490A JP9076490A JPH03287726A JP H03287726 A JPH03287726 A JP H03287726A JP 9076490 A JP9076490 A JP 9076490A JP 9076490 A JP9076490 A JP 9076490A JP H03287726 A JPH03287726 A JP H03287726A
- Authority
- JP
- Japan
- Prior art keywords
- less
- quenching
- cold
- toughness
- steel sheet
- 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.)
- Granted
Links
- 229910000712 Boron steel Inorganic materials 0.000 title claims abstract description 7
- 238000004519 manufacturing process Methods 0.000 title claims description 5
- 238000010791 quenching Methods 0.000 claims abstract description 43
- 230000000171 quenching effect Effects 0.000 claims abstract description 39
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims abstract description 13
- 229910000831 Steel Inorganic materials 0.000 claims abstract description 11
- 239000010959 steel Substances 0.000 claims abstract description 11
- 239000012535 impurity Substances 0.000 claims abstract description 4
- 238000005482 strain hardening Methods 0.000 claims abstract description 4
- 238000010438 heat treatment Methods 0.000 claims description 10
- 238000005097 cold rolling Methods 0.000 claims description 9
- 238000005098 hot rolling Methods 0.000 claims description 2
- 229910052799 carbon Inorganic materials 0.000 abstract description 6
- 238000000034 method Methods 0.000 abstract description 5
- 239000000203 mixture Substances 0.000 abstract description 5
- 229910052796 boron Inorganic materials 0.000 abstract description 4
- 238000005096 rolling process Methods 0.000 abstract 1
- 239000000463 material Substances 0.000 description 9
- 238000000137 annealing Methods 0.000 description 8
- 229910001566 austenite Inorganic materials 0.000 description 5
- 238000005336 cracking Methods 0.000 description 5
- 238000005496 tempering Methods 0.000 description 4
- 229910001567 cementite Inorganic materials 0.000 description 3
- 238000007796 conventional method Methods 0.000 description 3
- 230000007423 decrease Effects 0.000 description 3
- KSOKAHYVTMZFBJ-UHFFFAOYSA-N iron;methane Chemical compound C.[Fe].[Fe].[Fe] KSOKAHYVTMZFBJ-UHFFFAOYSA-N 0.000 description 3
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 229910052738 indium Inorganic materials 0.000 description 2
- 229910000734 martensite Inorganic materials 0.000 description 2
- 238000001000 micrograph Methods 0.000 description 2
- 238000005279 austempering Methods 0.000 description 1
- 238000003776 cleavage reaction Methods 0.000 description 1
- 239000010960 cold rolled steel Substances 0.000 description 1
- 239000002131 composite material Substances 0.000 description 1
- 239000000446 fuel Substances 0.000 description 1
- 239000004615 ingredient Substances 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 150000001247 metal acetylides Chemical class 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 238000003825 pressing Methods 0.000 description 1
- 230000007017 scission Effects 0.000 description 1
- 230000035945 sensitivity Effects 0.000 description 1
- 239000002436 steel type Substances 0.000 description 1
Landscapes
- Heat Treatment Of Steel (AREA)
- Heat Treatment Of Sheet Steel (AREA)
- Heat Treatment Of Articles (AREA)
Abstract
Description
【発明の詳細な説明】
〔産業上の利用分野〕
本発明は、自動車用強度部材（シートベルト金具等）に
好適な、冷間加工性、焼入性、靭性に優れたボロン鋼板
に関する。DETAILED DESCRIPTION OF THE INVENTION [Industrial Application Field] The present invention relates to a boron steel sheet with excellent cold workability, hardenability, and toughness, suitable for automotive strength members (seat belt fittings, etc.).
自動車用強度部材等は、熱延鋼板又は冷延鋼板を複雑な
形状に冷間ブレス加工した後、焼入れ焼戻し、オーステ
ンパーなどの熱処理を施されて製造される。Automotive strength members and the like are manufactured by cold-pressing a hot-rolled steel plate or a cold-rolled steel plate into a complicated shape, and then subjecting it to heat treatment such as quenching, tempering, and austempering.
このため、素材に対し、冷間加工性、焼入性、熱処理後
の高強度（１４０ｋｇ／ｍｍ２程度、Ｈ，Ｃ＝４２〜４
６）、高靭性が要求される。For this reason, the material has high cold workability, hardenability, and high strength after heat treatment (approximately 140 kg/mm2, H, C = 42 to 4
6) High toughness is required.
特に近年、自動車業界では、燃費向上のため部品の軽量
化の要請が高く、これに対応するため、より高強度化の
傾向にあるが、従来一般に使用されている素材（鋼種Ｓ
５５ ＣＭ）では、強度か高くなるにしたがい、切下
感受性が高まり靭性が低下する。従って従来、上記要請
を満足する高強度でかつ高靭性を併有した鋼板はなかっ
た。Particularly in recent years, there has been a strong demand in the automobile industry for parts to be made lighter in order to improve fuel efficiency, and to meet this demand, there has been a trend towards higher strength.
55 CM), as the strength increases, the undercut sensitivity increases and the toughness decreases. Therefore, conventionally, there has been no steel plate that has both high strength and high toughness that satisfies the above requirements.
一般に、素材の強度（硬度）と加工性とは両立が困難で
ある場合が多い。たとえば、鋼種Ｓ５５ＣＭは、焼入焼
戻し後の強度を確保するため［Ｃ］量は、０．５２〜０
．５８％と高めとしである。Generally, it is often difficult to achieve both strength (hardness) and workability of a material. For example, for steel type S55CM, the amount of [C] is 0.52 to 0 to ensure strength after quenching and tempering.
．． It is high at 58%.
したがって、十分な冷間加工性を得るために、素材の硬
度をＨＲＢ≦８２に下げようとすると、冷間圧延、焼鈍
、冷間圧延、焼鈍と２回づつ繰り返し、セメンタイトの
球状化を図らねばならない。Therefore, in order to reduce the hardness of the material to HRB≦82 in order to obtain sufficient cold workability, it is necessary to repeat cold rolling, annealing, cold rolling, and annealing twice to make the cementite spheroidal. It won't happen.
このように工程が複雑であるために、素材の製造コスト
は高くなる。Since the process is complicated in this way, the manufacturing cost of the material is high.
また、８５５ＣＭは、通常、焼入れ焼戻しして硬度をＨ
１１Ｃ＝４２〜４６（引張強さ１４０〜１６０ ｋｇ／
ｍｍ２）に調質される。このように焼入処理と焼戻し処
理の双方を行う必要があるので、熱処理コストが高いば
かりでなく、前述のように、［Ｃ］量が高いので、水焼
入では焼割れしやすいため、油焼入れしなければならず
熱処理コストが高い。さらに、［Ｃ］量が高いため、焼
入時のマルテンサイト中に固溶する［Ｃ］量が多く、焼
入歪が発生しやすいという問題点もある。In addition, 855CM is usually quenched and tempered to increase the hardness to H.
11C=42~46 (tensile strength 140~160 kg/
mm2). Since it is necessary to perform both quenching treatment and tempering treatment in this way, not only is the heat treatment cost high, but also, as mentioned above, since the amount of [C] is high, water quenching is prone to quench cracking, so oil It must be hardened and the heat treatment cost is high. Furthermore, since the amount of [C] is high, the amount of [C] dissolved in martensite during quenching is large, and there is also the problem that quenching distortion is likely to occur.
さらに、８５５ＣＭは［Ｃ］量が高いため、焼戻し時に
旧オーステナイト粒界にフィルム状のセメンタイトが析
出し、旧オーステナイト粒界を脆化させるため、粒界破
壊しやすく、靭性が低い。Furthermore, since 855CM has a high [C] content, film-like cementite precipitates at the prior austenite grain boundaries during tempering, which embrittles the prior austenite grain boundaries, resulting in easy intergranular fracture and low toughness.
そこで本発明の主たる目的は、冷間圧延、焼鈍回数が少
なくても、素材の硬さが低く、冷間加工性に優れ、水焼
入可能でかつ、焼入ままでも歪の発生が少なく、希望す
る硬さが得られ、靭性の優れたボロン鋼板を提供するこ
とにある。Therefore, the main purpose of the present invention is to provide a material with low hardness, excellent cold workability, water quenching, and low distortion even after quenching even if the number of cold rolling and annealing is small. The objective is to provide a boron steel plate with desired hardness and excellent toughness.
上記課題は、Ｃ：０．１５％以上０．４０％未満、Ｓｉ
：０．５０％未満、Ｍｎ：０．６０％以上１．５０未満
、Ｂ ： ０．０００５％以上０．００３０％未満を含
有し、残部Ｆｅおよび不可避的不純物からなる鋼を、板
厚６．０闘以下に熱間圧延又は冷間圧延した後、プレス
にて冷間加工し、次いで焼入温度８５０℃以上９５０℃
未満で加熱し、焼入強烈度０．３５ｃｍ−’以上１．５
０ｃｍ ’未満で水焼入することで解決される。The above issues are C: 0.15% or more and less than 0.40%, Si
: less than 0.50%, Mn: 0.60% or more and less than 1.50, B: 0.0005% or more and less than 0.0030%, and the balance is Fe and unavoidable impurities. After hot-rolling or cold-rolling to 0% or less, cold working in a press, and then quenching at a temperature of 850°C or higher and 950°C.
Heating at less than 0.35cm-', the quenching intensity is more than 1.5
This can be solved by water quenching at a depth of less than 0 cm'.
本発明では、上記組成の素材を用いるものであるから、
炭素濃度［Ｃ］を低く抑えているので、焼割れや焼入れ
歪が起こりにくい。In the present invention, since the material having the above composition is used,
Since the carbon concentration [C] is kept low, quench cracking and quenching distortion are less likely to occur.
また、冷間圧延−焼鈍各１回づつの工程でＨＲＢ≦８２
が得られるため、低コストで優れた冷間加工性を示すも
のとなる。In addition, HRB≦82 in each process of cold rolling and annealing.
Therefore, it exhibits excellent cold workability at low cost.
さらに、焼入ままで、ＨＲＣ＝４２〜４６の高硬度、ｖ
Ｔ、、＝−５５〜７０℃（３５５ＣＭでは約−２０℃）
の高靭性が得られる。Furthermore, as quenched, high hardness of HRC = 42 to 46, v
T,, = -55 to 70℃ (approximately -20℃ for 355CM)
High toughness can be obtained.
以下本発明をさらに具体的に説明する。 The present invention will be explained in more detail below.
本発明のボロン鋼板は、Ｃ：Ｏ，１５％以上０，４０％
未満、Ｓｉ：０．５０％未満、Ｍｎ：０．６０％以上１
．５０未満、Ｂ ： ０．０００５％以上０．００３０
％未満を含有し、残部Ｆｅおよび不可避的不純物からな
る鋼を、板厚６．０丁以下に熱間圧延又は冷間圧延した
後、プレスにて冷間加工し、次いで焼入温度８５０℃以
上９５０℃未満で加熱し、焼入強烈度０．３５ｃｍ ’
以上１．５０国″１未満で水焼入するで得ることができ
る。The boron steel sheet of the present invention has C:O, 15% or more and 0.40%
Si: less than 0.50%, Mn: 0.60% or more 1
．． Less than 50, B: 0.0005% or more 0.0030
%, the balance consisting of Fe and unavoidable impurities is hot-rolled or cold-rolled to a plate thickness of 6.0 mm or less, cold-worked in a press, and then quenched at a temperature of 850°C or higher. Heating below 950℃, quenching intensity 0.35cm'
It can be obtained by water quenching at less than 1.50 mm.
次に上記各製造条件の限定理由を説明する。Next, the reason for limiting each of the above manufacturing conditions will be explained.
［Ｃ］ ・０．１５％以上、０．４０％未満０、１５
％未満では水焼入ままで、ＨＲＣ＝ ４２以上確保でき
ず、０．４０％以上では、−回の冷間圧延−焼鈍工程で
ＨＲＢ≦８２確保できないとともに、焼入れ後粒界破壊
し、靭性悪くなる。[C] ・0.15% or more, less than 0.40% 0, 15
If it is less than 0.40%, it will not be possible to ensure HRC = 42 or more as it is water quenched, and if it is more than 0.40%, it will not be possible to ensure HRB ≦ 82 in the cold rolling-annealing process, and grain boundary fracture will occur after quenching, resulting in poor toughness. Become.
［Ｓｉコ 、 ０． ５ ０％未満
０５０％以上であると、焼入れ後高炭素マルテンサイト
が残留しやすく、靭性が悪くなる。[Sico, 0. If it is less than 50% and more than 50%, high carbon martensite tends to remain after quenching, resulting in poor toughness.
［Ｍｎ］ ； ０．６０％以上、１．５０％未満０．
６０％未満であると、焼入性が悪く、ＨＲＣ＝４２以上
確保できない。逆に１．５０％以上であると、水焼入れ
時、焼割れを起こしやすい。[Mn]; 0.60% or more, less than 1.50%0.
If it is less than 60%, hardenability is poor and HRC=42 or more cannot be secured. On the other hand, if it is 1.50% or more, quench cracking is likely to occur during water quenching.
［Ｂ］；０．０００５％以上、０．００３０％未満焼入
性のために０．０００５％以上であることは必要であり
、また、水焼入時に旧オーステナイト粒界にフィルム状
セメンタイトの析出を防止し、粒界脆化を防止するため
にも必要である。[B]: 0.0005% or more, less than 0.0030% A content of 0.0005% or more is necessary for hardenability, and also prevents the precipitation of film-like cementite at prior austenite grain boundaries during water quenching. It is also necessary to prevent grain boundary embrittlement.
０、００３０％以上であると、水焼入れ時、旧オーステ
ナイト粒界にＭｚ３（ＣＢ）６型、複合炭化物を析出さ
せ、却って粒界を脆化させる。If it is 0.0030% or more, Mz3(CB)6 type composite carbides are precipitated at the prior austenite grain boundaries during water quenching, and the grain boundaries are rather brittle.
板厚、 ６．００闘以下
６．００ａｍを超えると、冷間加工時の割れが発生しや
すくなるばかりでなく、焼きも入りにくくなり、希望の
硬さが得られない。If the plate thickness exceeds 6.00 am, it will not only be more likely to crack during cold working, but also difficult to harden, making it impossible to obtain the desired hardness.
焼入温度；８５０℃以上、９５０℃未満８５０℃未満で
は、完全にオーステナイト化されず、焼入後、靭性が低
下する。９５０℃以上では、オーステナイト粒が粗大化
し、靭性が低下する。Quenching temperature: 850°C or more, less than 950°C, and less than 850°C, the steel will not be completely austenitized and the toughness will decrease after quenching. At temperatures above 950°C, austenite grains become coarse and toughness decreases.
焼入強烈度Ｈ； ０．３５ （ｃｍ−’）以上、１．５
０（ｃｍ）未満
０、３５ （ｃｍ−’）未満（油焼入）では、焼きが入
らず所望の硬さが得られない。１．５０ （ｃｍ−’）
以上では、焼割れが発生する。Hardening intensity H: 0.35 (cm-') or more, 1.5
If the hardness is less than 0 (cm) or less than 35 (cm-') (oil quenching), quenching will not occur and the desired hardness will not be obtained. 1.50 (cm-')
Above this, quench cracking occurs.
次に実施例により、本発明の効果を明らかにする。 Next, examples will clarify the effects of the present invention.
（実施例１）
第１図に示すように、素材の硬度ＨＲＢ値を、成分中の
［Ｃ］量を変化させるとともに、冷間圧延−焼鈍を本発
明にしたがって一回のみ行った場合と同工程を２回繰り
返した場合とで比較して調べたところ、本発明では従来
法より［Ｃ］量の低い状態で、従来と同様の低いＨ，Ｂ
値を発揮することがわかった。なお、この場合の他の成
分組成は次の通りである。(Example 1) As shown in Fig. 1, the hardness HRB value of the material was changed to the same value as when cold rolling and annealing were performed only once according to the present invention while changing the amount of [C] in the component. A comparison study with the case where the process was repeated twice revealed that in the present invention, the amount of [C] was lower than that of the conventional method, but the amount of H and B was as low as that of the conventional method.
It was found that it has great value. The other component compositions in this case are as follows.
５ｉ＝０．２０〜０．２５％
Ｍｎ＝０．８５〜０．９０％
Ｂ 〜０．０００８〜０．００１２％（実施例２）
また、Ｂ量および［Ｃ］量を変えて、熱処理後のＨＲＣ
について調べたところ、第２図の結果が得られた。5i=0.20-0.25% Mn=0.85-0.90% B ~0.0008-0.0012% (Example 2) Also, by changing the amount of B and the amount of [C], after heat treatment HRC of
When we investigated this, we obtained the results shown in Figure 2.
同図から、焼入れ硬さはＢ量が比較的高い場合が優れて
いることが判る。また、低い［Ｃ］量で目的のＨＲＣ値
を得ることができることも判る。From the same figure, it can be seen that the quenching hardness is better when the amount of B is relatively high. It is also seen that the desired HRC value can be obtained with a low [C] amount.
ただし、他の成分量は、次の通りである。However, the amounts of other ingredients are as follows.
５ｉ＝０．２０〜０．２５％
Ｍｎ＝０．８５〜０．９０％
また、熱処理としては、８９０℃→水焼入を行った（焼
入強烈度Ｈ＝ ０．５０ ｃｍ−’）（実施例３）
さらに、第３図に示すように、焼入歪みを小さくするた
めには、［Ｃ］量を低（することが有効であることか判
明した。この場合、他の成分等は下記の通りである。5i = 0.20-0.25% Mn = 0.85-0.90% In addition, as heat treatment, water quenching was performed at 890°C (quenching intensity H = 0.50 cm-') ( Example 3) Furthermore, as shown in Fig. 3, it was found that it is effective to reduce the amount of [C] in order to reduce the quenching distortion. In this case, other components, etc. It is as follows.
５ｉ＝０．２０〜０．２５％
Ｍｎ＝０．８５〜０．９０％
また、熱処理としては、８９０℃→水焼入を行った（焼
入強烈度Ｈ＝０．５０国−１）（実施例４）
鋼成分、板厚および焼入れ温度を種々変えて、得られた
鋼板の特性を調べたところ、第１表の結果を得た。5i = 0.20 to 0.25% Mn = 0.85 to 0.90% In addition, as heat treatment, water quenching was performed at 890°C (quenching intensity H = 0.50 country - 1) ( Example 4) The properties of the obtained steel plates were investigated by varying the steel composition, plate thickness, and quenching temperature, and the results shown in Table 1 were obtained.
上記第１表から明らかなように、本発明によれば、■冷
間圧延−焼鈍各１回づつの工程で、Ｈ１ｌＢ≦８２が得
られ、低コストで優れた冷間加工性を有する、■焼入ま
まで、ＨＲＣ＝４２〜４６の高硬度１．Ｔ、、−−５５
〜−７０℃という高靭性値が得られる（粒界破壊せず、
へき界破壊のみであるため）、■［Ｃ］量が低いため、
焼割れ、焼入歪みが起こりにくい等の各種利点を有する
ことが判る。As is clear from Table 1 above, according to the present invention, H11B≦82 can be obtained in each step of cold rolling and annealing, and excellent cold workability is achieved at low cost. High hardness of HRC=42-46 as quenched 1. T,, --55
A high toughness value of ~-70°C can be obtained (no grain boundary fracture,
■ Because the amount of [C] is low,
It can be seen that it has various advantages such as less quenching cracking and quenching distortion.
さらに、本発明鋼板の破断面の顕微鏡写真（倍率１００
０倍）を第４図（ａ）、従来例の破断面を第４図１ｂ）
に示す。Furthermore, a micrograph of the fracture surface of the steel plate of the present invention (magnification: 100
0x) is shown in Figure 4 (a), and the fracture surface of the conventional example is shown in Figure 4 (1b).
Shown below.
本発明例では粒内破壊のへき開破面であるのに対し、従
来例では粒界破壊であることが判る。これにより、本発
明鋼板は高靭性を有するが推測できよう。It can be seen that the example of the present invention is a cleavage fracture surface due to intragranular fracture, whereas the conventional example is a intergranular fracture. From this, it can be inferred that the steel sheet of the present invention has high toughness.
以上の通り、本発明によれば、冷間圧延、焼鈍回数が少
なくても、素材の硬さが低く、冷間加工性に優れ、水焼
入可能でかつ、焼入ままでも歪の発生が少なく、希望す
る硬さが得られ、靭性の優れた材料を提供することがで
きる。As described above, according to the present invention, even if the number of times of cold rolling and annealing is small, the material has low hardness, excellent cold workability, water quenching, and no distortion even after quenching. It is possible to provide a material with a desired hardness and excellent toughness.
第１図は本発明における［Ｃ］量に対するＨＲＢ値を従
来法と比較して示したグラフ、第２図はＨ，Ｃ値を示し
たグラフ、第３図は［Ｃ］量に対する焼入歪を示したグ
ラフ、第４図（ａｌ、 （ｂ）は、それぞれ本発明例、
従来例の鋼板の破断面の金属組織の顕微鏡写真（いずれ
も倍率は１，０００倍）である。
第１図
第
図
（Ｃ）
第２図
（Ｃ）Figure 1 is a graph showing the HRB value versus the amount of [C] in the present invention in comparison with the conventional method, Figure 2 is a graph showing the H and C values, and Figure 3 is the quenching strain versus the amount of [C]. The graphs shown in FIGS. 4 (al) and (b) are the examples of the present invention,
These are micrographs (all magnifications are 1,000x) of the metal structure of the fractured surface of a conventional steel plate. Figure 1 (C) Figure 2 (C)
Claims (1)
５０％未満、Ｍｎ：０．６０％以上１．５０未満、Ｂ：
０．０００５％以上０．００３０％未満を含有し、残部
Ｆｅおよび不可避的不純物からなる鋼を、板厚６．０ｍ
ｍ以下に熱間圧延又は冷間圧延した後、プレスにて冷間
加工し、次いで焼入温度８５０℃以上９５０℃未満で加
熱し、焼入強烈度０．３５ｃｍ＾−＾１以上１．５０ｃ
ｍ＾−＾１未満で水焼入することを特徴とするボロン鋼
板の製造方法。(1) C: 0.15% or more and less than 0.40%, Si: 0.
Less than 50%, Mn: 0.60% or more and less than 1.50, B:
A steel containing 0.0005% or more and less than 0.0030%, with the balance consisting of Fe and unavoidable impurities, was made into a plate with a thickness of 6.0 m.
After hot rolling or cold rolling to less than m, cold working in a press, then heating at a quenching temperature of 850°C or more and less than 950°C, to achieve a quenching intensity of 0.35cm^-^1 or more and 1.50cm.
A method for producing a boron steel sheet, characterized by water quenching at less than m^-^1.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP9076490A JPH07103420B2 (en) | 1990-04-05 | 1990-04-05 | Method for manufacturing member made of boron steel plate |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP9076490A JPH07103420B2 (en) | 1990-04-05 | 1990-04-05 | Method for manufacturing member made of boron steel plate |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH03287726A true JPH03287726A (en) | 1991-12-18 |
| JPH07103420B2 JPH07103420B2 (en) | 1995-11-08 |
Family
ID=14007674
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP9076490A Expired - Lifetime JPH07103420B2 (en) | 1990-04-05 | 1990-04-05 | Method for manufacturing member made of boron steel plate |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH07103420B2 (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| DE102016219278A1 (en) * | 2016-10-05 | 2018-04-05 | Bayerische Motoren Werke Aktiengesellschaft | Process for producing a high-strength tube part |
-
1990
- 1990-04-05 JP JP9076490A patent/JPH07103420B2/en not_active Expired - Lifetime
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| DE102016219278A1 (en) * | 2016-10-05 | 2018-04-05 | Bayerische Motoren Werke Aktiengesellschaft | Process for producing a high-strength tube part |
| US11131002B2 (en) | 2016-10-05 | 2021-09-28 | Bayerische Motoren Werke Aktiengesellschaft | Method for producing a high strength tube part |
Also Published As
| Publication number | Publication date |
|---|---|
| JPH07103420B2 (en) | 1995-11-08 |
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