JP2777416B2 - Connecting member - Google Patents
Connecting memberInfo
- Publication number
- JP2777416B2 JP2777416B2 JP21097789A JP21097789A JP2777416B2 JP 2777416 B2 JP2777416 B2 JP 2777416B2 JP 21097789 A JP21097789 A JP 21097789A JP 21097789 A JP21097789 A JP 21097789A JP 2777416 B2 JP2777416 B2 JP 2777416B2
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- JP
- Japan
- Prior art keywords
- connecting member
- atomic
- amorphous alloy
- members
- alloy
- 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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- Insertion Pins And Rivets (AREA)
Description
【発明の詳細な説明】 ［産業上の利用分野］ 本発明は、加工が容易で且つ高強度なリベット等とし
て利用される非晶質合金材料を用いた連結部材に関す
る。Description: TECHNICAL FIELD The present invention relates to a connecting member using an amorphous alloy material which is easy to process and is used as a high-strength rivet or the like.
［従来技術］ 例えば、金属の板材同士を連結する連結部材としてリ
ベットがある。このリベットは、通常、板材のリベット
孔に挿通し、その端部を塑性変形させることで板材同士
を締結するものである。リベットの素材としては、従
来、鋼材、アルミニウム合金材、黄銅材等が用いられて
いる。[Prior Art] For example, there is a rivet as a connecting member for connecting metal plate members. The rivet is usually inserted into a rivet hole of a plate material, and the ends thereof are plastically deformed to fasten the plate materials. Conventionally, steel, aluminum alloy, brass, and the like have been used as rivet materials.
［発明が解決しようとする課題］ ところで、従来のリベットは塑性変形をさせるために
相当な力を必要とする。また、リベットをこのようにし
て塑性変形させることで連結された板材は、前記リベッ
トを塑性変形させる力以上の外力が付与された場合にリ
ベットが破壊され分離してしまう。さらには、板材を分
離する際に、リベットを破壊しなければならず、そのた
めにも板材も損壊される虞がある。[Problems to be Solved by the Invention] By the way, the conventional rivet requires a considerable force to cause plastic deformation. Moreover, the plate material connected by plastically deforming the rivet in this manner is broken and separated when an external force greater than the force for plastically deforming the rivet is applied. Furthermore, when separating the plate material, the rivet must be broken, which may damage the plate material.
本発明は前記の課題を解決するためになされたもので
あって、加工等が極めて容易であり、しかも、部材同士
を高強度に連結することが出来、さらには、取り外しが
簡便で前記部材を容易に分離することの出来る連結部材
を提供することを目的とする。The present invention has been made in order to solve the above-mentioned problems, processing and the like are extremely easy, and furthermore, the members can be connected to each other with high strength. An object is to provide a connecting member that can be easily separated.
［課題を解決するための手段］ 前記の課題を解決するために、本発明は、部材同士を
連結する連結部材において、AlまたはMgと、希土類元素
とを含み、少なくとも３種類以上の元素を配合してなる
非晶質合金材料を用いることを特徴とする。[Means for Solving the Problems] In order to solve the above problems, the present invention provides a connecting member for connecting members, which contains at least three or more elements containing Al or Mg and a rare earth element. It is characterized by using an amorphous alloy material formed as described above.
前記連結部材において、好適には、非晶質合金材料
は、Alを25〜85原子％と、NiおよびCoから選ばれる少な
くとも１種の元素を５〜25原子％と、希土類元素から選
ばれる少なくとも１種の元素を６〜50原子％とを配合し
てなり、少なくとも体積率で50％以上の非晶質を含むも
のとする。In the connection member, preferably, the amorphous alloy material includes Al of 25 to 85 atomic%, at least one element selected from Ni and Co of 5 to 25 atomic%, and at least one selected from rare earth elements. One element is blended with 6 to 50 atomic% and contains at least 50% or more amorphous by volume.
また、前記連結部材において、非晶質合金材料は、Al
を75〜85原子％と、NiおよびCoから選ばれる少なくとも
１種の元素を５〜10原子％と、希土類元素から選ばれる
少なくとも１種の元素を５〜12原子％と、ＢおよびＣか
ら選ばれる少なくとも１種の元素を0.5〜５原子％とを
配合してなり、少なくとも体積率で50％以上の非晶質を
含むものを用いることができる。Further, in the connecting member, the amorphous alloy material is Al
75 to 85 atomic%, at least one element selected from Ni and Co is 5 to 10 atomic%, at least one element selected from rare earth elements is 5 to 12 atomic%, and selected from B and C At least one element is mixed with 0.5 to 5 atomic%, and an element containing at least 50% or more of amorphous by volume ratio can be used.
さらに、本発明は、部材同士を連結する連結部材にお
いて、Siと、Fe、CoおよびNiから選ばれる少なくとも１
種の元素と、Ｂとを配合してなる非晶質合金材料を用い
ることを特徴とする。Furthermore, the present invention provides a connecting member for connecting members, wherein at least one selected from Si, Fe, Co and Ni is used.
It is characterized in that an amorphous alloy material obtained by blending B with a seed element is used.
［作用］ 本発明は連結部材は、AlまたはMgと、希土類元素とを
含む３種類以上の元素からなり、溶融化温度よりも低い
ガラス転移温度で軟化する特性を備える。この連結部材
を前記ガラス転移温度まで加熱して変形させることで部
材同士を連結させ冷却すれば、前記部材同士を高強度に
連結することが出来る。また、前記連結部材をガラス転
移温度まで再び加熱すれば当該部材の分離も容易であ
る。[Action] In the present invention, the connection member is made of three or more elements including Al or Mg and a rare earth element, and has a property of softening at a glass transition temperature lower than the melting temperature. If the connecting members are connected and cooled by heating and deforming the connecting members to the glass transition temperature, the members can be connected with high strength. Further, if the connecting member is heated again to the glass transition temperature, the member can be easily separated.
また、本発明の連結部材は、Fe、CoまたはNiと、Si
と、Ｂとを含む３種類以上の元素からなり、溶融化温度
よりも低いガラス転移温度で軟化する特性を備える。こ
の連結部材を用いて、同様に、部材同士の連結・分離を
容易に行うことが出来る。Further, the connecting member of the present invention, Fe, Co or Ni, and Si
And B, and has the property of softening at a glass transition temperature lower than the melting temperature. Similarly, the connection and separation of the members can be easily performed using this connection member.
［実施例］ 本発明に係る連結部材について実施例を挙げ、添付の
図面を参照しながら以下詳細に説明する。[Example] An example of a connecting member according to the present invention will be described below in detail with reference to the accompanying drawings.
第１図ａは本発明に係る連結部材としてのリベット10
と、前記リベット10によって連結される第１板材12およ
び第２板材14を示す。第１および第２板材12、14はリベ
ット10を挿通するための孔部12a,14aを有している。こ
の場合、リベット10をこれらの孔部12a、14aに挿通し、
その端部を塑性変形させることにより、第１図ｂに示す
ように、第１および第２板材12、14の連結が実現され
る。FIG. 1a shows a rivet 10 as a connecting member according to the present invention.
And a first plate 12 and a second plate 14 connected by the rivet 10. The first and second plate members 12 and 14 have holes 12a and 14a through which the rivet 10 is inserted. In this case, insert the rivet 10 into these holes 12a, 14a,
By plastically deforming the ends, the connection of the first and second plate members 12, 14 is realized as shown in FIG. 1b.
ここで、リベット10は、化学式AlaMbRcXdで表される
非晶質合金によって構成される。この場合、Ｍとして
は、NiとCoとが選択的に用いられ、Ｒとしては希土類元
素の中、ＹとCeとLaとが選択的に採用される。また、Ｘ
としては、ｄ≠０の場合においてＢとＣとが選択的に添
加される。Here, the rivet 10 is made of an amorphous alloy represented by a chemical formula of Al a M b R c X d . In this case, as M, Ni and Co are selectively used, and as R, Y, Ce and La are selectively adopted among rare earth elements. Also, X
In the case where d ≠ 0, B and C are selectively added.
次に、このような非晶質合金の特性を説明する。 Next, characteristics of such an amorphous alloy will be described.
そこで、高周波溶解により所定の成分組成を有する溶
融金属を生成し、この溶融金属を急冷凝固させて帯状の
非晶質合金を得る。この種の冷却方法としては、高速回
転する金属製ロールに溶融金属を吹き付ける回転ロール
法、液中に溶融金属を噴出させる液中紡糸法およびガラ
ス管中の溶融金属をこのガラス管とともに引張するテー
ラー法、アトマイズ法等が知られている。Thus, a molten metal having a predetermined component composition is generated by high frequency melting, and the molten metal is rapidly solidified to obtain a strip-shaped amorphous alloy. Examples of this type of cooling method include a rotating roll method in which molten metal is sprayed onto a metal roll that rotates at high speed, a submerged spinning method in which molten metal is ejected into liquid, and a tailor that pulls molten metal in a glass tube together with the glass tube A method and an atomizing method are known.
このようにして得られた各種非晶質合金について、硬
度試験（HV）並びに密着曲げ試験が行われ、表１に示さ
れるような結果が得られた。硬度は、実質的にマイクロ
ビッカーズ硬度計を用いて測定した。また、密着曲げ試
験では、所定長の非晶質合金を折り曲げてその両端部が
密着した状態で前記非晶質合金が破断しなければ、密着
曲げ可能であるとする。この場合には、表１において曲
げ可能であるとき、「○」で表され、一方、亀裂等が発
生したときには「△」、さらに破断したときは「×」で
表される。A hardness test (HV) and a contact bending test were performed on the various amorphous alloys thus obtained, and the results shown in Table 1 were obtained. Hardness was substantially measured using a Micro Vickers hardness tester. Further, in the close contact bending test, if the amorphous alloy of a predetermined length is bent and the amorphous alloy is not broken in a state where both ends thereof are in close contact with each other, it is assumed that close contact bending is possible. In this case, in Table 1, when it is bendable, it is represented by “○”, on the other hand, when a crack or the like occurs, it is represented by “△”, and when it is further broken, it is represented by “×”.
なお、表１中、No.1乃至No.12に示すように、NiとＹ
の原子パーセントを一定にしてＢおよびＣを夫々所定の
原子パーセント添加すると、前記ＢおよびＣを含まない
非晶質合金（No.1）に較べ硬度が大きくなっている。同
様に、No.13、No.18、No.21、No.29、No.33、No.35およ
びNo.39と同一のＭおよびＲ元素を同一の原子パーセン
トずつ含む各非晶質合金にＢまたＣを添加させることに
より、硬度の向上が図られることになる。 In Table 1, as shown in No. 1 to No. 12, Ni and Y
When B and C are added at a predetermined atomic percentage while keeping the atomic percentage constant, the hardness is higher than that of the amorphous alloy containing no B and C (No. 1). Similarly, for each amorphous alloy containing the same M and R elements as the same atomic percentages as No. 13, No. 18, No. 21, No. 29, No. 33, No. 35 and No. 39, By adding B or C, the hardness is improved.
その際、No.2、No.22およびNo.40に示すように、Ｂを
１原子パーセントだけ添加したものでは、硬度において
十分でない場合も考えられ、従って、Ｂを実質的に２原
子パーセント以上含ませるものが好ましい。At this time, as shown in No. 2, No. 22 and No. 40, it is conceivable that the addition of 1 atomic percent of B may not be sufficient in hardness, so that B is substantially 2 atomic percent or more. What is included is preferred.
また、No.8では、硬度の向上が著しい一方、密着曲げ
試験が不良、すなわち、剛性が劣るものとなっている。
このため、Ｂを実質的に10原子パーセント以下、より好
適には、８原子パーセント以下に限定すれば、高強度且
つ高剛性を有する非晶質合金が得られることになる。In No. 8, while the hardness was remarkably improved, the adhesion bending test was poor, that is, the rigidity was poor.
Therefore, if B is substantially limited to 10 atomic percent or less, more preferably, 8 atomic percent or less, an amorphous alloy having high strength and high rigidity can be obtained.
次に、A1−Ni−Ｙ系合金、すなわち、AlaNibYc合金の
組成図を第２図に示す。ここで、図中、SgはAlaNibYc合
金がある温度で急激に軟化する、所謂、ガラス転移が生
起される組成範囲である。従って、この範囲内で夫々の
原子パーセントを選択されたNiおよびＹを含む非晶質合
金を一旦そのガラス転移温度まで加温させれば、前記非
晶質合金が急激に軟化するため、所定の部品形状に対応
して容易に成形することが出来る。Next, FIG. 2 shows a composition diagram of the A1-Ni-Y alloy, that is, the Al a Ni b Y c alloy. Here, in the figure, Sg is a composition range in which the so-called glass transition occurs, in which the Al a Ni b Y c alloy softens rapidly at a certain temperature. Therefore, once the amorphous alloy containing Ni and Y whose respective atomic percentages are selected within this range is once heated to its glass transition temperature, the amorphous alloy softens rapidly, so It can be easily formed according to the part shape.
表２にNo.1のAl85Ni5Y10合金（上段）について加熱温
度と硬さ（HV）との関係および比較例であるAl85Ni10Y5
合金（下段）のデータを示す。Table 2 shows the relationship between the heating temperature and the hardness (HV) for the No. 1 Al 85 Ni 5 Y 10 alloy (upper row) and Al 85 Ni 10 Y 5 which is a comparative example.
The data for the alloy (lower) is shown.
この場合、Al85Ni5Y10合金では、加熱温度260〜280℃
（Sg範囲）において軟化現象が表れている。これに対し
てAl85Ni10Y5合金では顕著な軟化現象が生じなく、ガラ
ス転移が発生していない。なお、Al85Ni5Y10合金の場合
の溶融化温度は280℃以上であり、上記Sg範囲では非晶
質状態（50％以上）が好適に維持される。 In this case, for Al 85 Ni 5 Y 10 alloy, the heating temperature is 260-280 ° C.
(Sg range) shows a softening phenomenon. On the other hand, in the Al 85 Ni 10 Y 5 alloy, no remarkable softening phenomenon occurs, and no glass transition occurs. The melting temperature of the Al 85 Ni 5 Y 10 alloy is 280 ° C. or higher, and the amorphous state (50% or higher) is suitably maintained in the Sg range.
また、AlaNibYc合金にＢまたはＣを所定の原子パーセ
ントだけ添加させた場合、実質的にSg範囲（ガラス転移
範囲）が拡大するという効果が得られる。Further, when B or C is added to the Al a Ni b Y c alloy by a predetermined atomic percent, an effect of substantially expanding the Sg range (glass transition range) is obtained.
第３図に、第２図中、実線に示すSd範囲（延性範囲）
に属するAl80Ni10Y5B5合金からなる試験用帯状合金を用
いて熱分析を行った結果を示す。FIG. 3 shows the Sd range (ductile range) indicated by the solid line in FIG.
4 shows the results of a thermal analysis performed using a test strip alloy composed of an Al 80 Ni 10 Y 5 B 5 alloy belonging to the group No.
第３図において、第１の発熱ピークの直前に吸熱反応
が発生している。これはAl80Ni10Y5B5合金が結晶化する
前に急激に軟化するためであり、この時の温度（287.3
℃）がガラス転移温度に相当する。In FIG. 3, an endothermic reaction occurs just before the first exothermic peak. This is because the Al 80 Ni 10 Y 5 B 5 alloy softens rapidly before crystallization, and the temperature (287.3
° C) corresponds to the glass transition temperature.
従って、Ｂを５原子パーセント添加させることによっ
て、Sd範囲（延性範囲）にまで実質的にSg範囲（ガラス
転移範囲）が拡大するに至る。ここで、Sd範囲とは、第
２図中、実線に示すように、 45≦4b＋5c≦100 （但し、０＜ｂ≦16、２≦ｃ≦12） であり、特に、 45≦4b＋5c≦100 （但し、ｂ≧ｃ、ｂ≦16、２≦ｃ） は一般的なAl−Ni−Ｙ系合金ではガラス転移が発生しな
い範囲を示す。Therefore, by adding 5 atomic percent of B, the Sg range (glass transition range) is substantially expanded to the Sd range (ductility range). Here, the Sd range is 45 ≦ 4b + 5c ≦ 100 (where 0 <b ≦ 16, 2 ≦ c ≦ 12) as shown by the solid line in FIG. 2, and particularly, 45 ≦ 4b + 5c ≦ 100 ( Here, b ≧ c, b ≦ 16, and 2 ≦ c) indicate a range in which glass transition does not occur in a general Al—Ni—Y alloy.
これによって、比較的広範囲にわたり成形性に優れた
非晶質合金を選択的に得ることが出来る。Thereby, an amorphous alloy excellent in formability can be selectively obtained over a relatively wide range.
さらに、上述したガラス転移を示す非晶質合金として
表３に示すものが挙げられる。Further, the amorphous alloys exhibiting the above-mentioned glass transition include those shown in Table 3.
以上のように、ガラス転移を示す非晶質合金を用いて
リベット10を製造した場合、極めて優れた効果が得られ
る。 As described above, when the rivet 10 is manufactured using an amorphous alloy exhibiting a glass transition, an extremely excellent effect can be obtained.
すなわち、例えば、Al85Ni5Y10合金からなるリベット
10を第１および第２の板材12、14の孔部12a、14aに挿通
して260乃至280℃に加熱し、塑性変形させる。この場
合、リベット10の硬度は、表２に示すように、５乃至20
kgf/mm2に低下しているため、その塑性変形は極めて容
易である。That is, for example, a rivet made of Al 85 Ni 5 Y 10 alloy
10 is inserted into the holes 12a and 14a of the first and second plate members 12 and 14 and heated to 260 to 280 ° C. to be plastically deformed. In this case, the hardness of the rivet 10 is 5 to 20 as shown in Table 2.
Since it has decreased to kgf / mm 2 , its plastic deformation is extremely easy.
次に、このリベット10を冷却すれば室温において120k
gf/mm2まで硬度が回復するため、第１および第２板材1
2、14が十分な締結力で連結されることになる。なお、
リベット10を塑性変形させる時の加熱温度Al85Ni5Y10合
金の溶融化温度以下にすることが出来るため、非晶質の
割合が加熱によっても十分に維持される。従って、リベ
ット10の硬度が低下することはない。Next, if this rivet 10 is cooled,
the hardness is restored to gf / mm 2, first and second plate members 1
2, 14 will be connected with sufficient fastening force. In addition,
Since the heating temperature at which the rivet 10 is plastically deformed can be lower than the melting temperature of the Al 85 Ni 5 Y 10 alloy, the amorphous ratio can be sufficiently maintained by heating. Therefore, the hardness of the rivet 10 does not decrease.
第４図は本発明に係る連結部材の他の実施例を示す。
この場合、第１部材16と第２部材18とは連結部材20によ
って連結される。すなわち、連結部材20はガラス転移温
度まで加熱され、軟化した状態で第１部材16の溝部16a
に第２部材18の凸状部18aとともに圧入される。次い
で、これらを冷却すれば、連結部材20の硬度が上昇し、
これによって第１および第２部材16、18が強固に連結さ
れることになる。締結時、または締結後、一部結晶化さ
せ、Tg温度近傍での強度を向上させる手続も可能であ
る。この場合、連結部材20を離脱させる時は、温度を上
げ、連結部材20の結晶化を進行させて脆化させ破壊す
る。FIG. 4 shows another embodiment of the connecting member according to the present invention.
In this case, the first member 16 and the second member 18 are connected by the connecting member 20. That is, the connecting member 20 is heated to the glass transition temperature, and in a softened state, the groove 16a of the first member 16 is formed.
Is pressed together with the convex portion 18a of the second member 18. Next, if these are cooled, the hardness of the connecting member 20 increases,
As a result, the first and second members 16, 18 are firmly connected. It is also possible to perform a procedure to partially crystallize at the time of fastening or after fastening to improve the strength near the Tg temperature. In this case, when the connecting member 20 is detached, the temperature is increased, the crystallization of the connecting member 20 proceeds, and the connecting member 20 is embrittled and broken.
なお、上述した実施例において、第１および第２板材
12、14あるいは第１および第２部材16、18を分離する場
合、再びガラス転移温度まで加熱すればその分離も容易
に行うことが出来る。In the embodiment described above, the first and second plate members are used.
When the members 12, 14 or the first and second members 16, 18 are separated, the members can be easily separated by heating to the glass transition temperature again.
［発明の効果］ 以上のように、本発明に係る連結部材は、溶融化温度
よりも低い温度で軟化するガラス転移温度を有する非晶
質合金で構成されている。従って、この連結部材をガラ
ス転移温度まで加熱することで、非晶質合金の特性を何
ら劣化させることなく軟化させることが出来、これによ
って部材同士の連結のための加工等の作業が極めて容易
となる。また、この連結部材を冷却すれば非晶質合金の
有する十分な強度を得ることが出来、部材同士の連結が
確実なものとなる。さらに、連結部材を再びガラス転移
温度まで加熱して軟化させれば、部材同士を分離するこ
とも容易である。[Effect of the Invention] As described above, the connecting member according to the present invention is made of an amorphous alloy having a glass transition temperature that softens at a temperature lower than the melting temperature. Therefore, by heating the connecting member to the glass transition temperature, it is possible to soften the amorphous alloy without deteriorating the characteristics of the amorphous alloy at all, thereby making it extremely easy to perform operations such as processing for connecting the members. Become. Further, if the connecting members are cooled, it is possible to obtain a sufficient strength of the amorphous alloy, and the connection between the members is ensured. Furthermore, if the connecting member is heated again to the glass transition temperature and softened, the members can be easily separated from each other.
第１図ａおよびｂは本発明に係る連結部材の第１実施例
の説明図、 第２図は本発明に係る連結部材を構成する非晶質合金の
一例の組成説明図、 第３図は本発明に係る連結部材を構成する非晶質合金の
一例の熱分析の説明図、 第４図は本発明に係る連結部材の第２実施例の説明図で
ある。 10……リベット、12、14……板材 16、18……部材、20……連結部材FIGS. 1a and 1b are explanatory views of a first embodiment of a connecting member according to the present invention, FIG. 2 is a composition explanatory view of an example of an amorphous alloy constituting a connecting member according to the present invention, FIG. FIG. 4 is an explanatory diagram of a thermal analysis of an example of an amorphous alloy constituting a connecting member according to the present invention. FIG. 4 is an explanatory diagram of a second embodiment of the connecting member according to the present invention. 10 ... rivets, 12, 14 ... plate materials 16, 18 ... members, 20 ... connecting members
Claims (4)
またはMgと、希土類元素とを含み、少なくとも３種類以
上の元素を配合してなる非晶質合金材料を用いることを
特徴とする連結部材。In a connecting member for connecting members, Al
Alternatively, a connecting member characterized by using an amorphous alloy material containing Mg and a rare earth element and containing at least three or more elements.
合金材料は、Alを25〜85原子％と、NiおよびCoから選ば
れる少なくとも１種の元素を５〜25原子％と、希土類元
素から選ばれる少なくとも１種の元素を６〜50原子％と
を配合してなり、少なくとも体積率で50％以上の非晶質
を含むことを特徴とする連結部材。2. The connecting member according to claim 1, wherein the amorphous alloy material comprises: 25 to 85 atomic% of Al; 5 to 25 atomic% of at least one element selected from Ni and Co; A connecting member comprising at least one element selected from elements and 6 to 50 atomic%, and containing at least 50% or more amorphous by volume.
合金材料は、Alを75〜85原子％と、NiおよびCoから選ば
れる少なくとも１種の元素を５〜10原子％と、希土類元
素から選ばれる少なくとも１種の元素を５〜12原子％
と、ＢおよびＣから選ばれる少なくとも１種の元素を0.
5〜５原子％とを配合してなり、少なくとも体積率で50
％以上の非晶質を含むことを特徴とする連結部材。3. The connecting member according to claim 1, wherein the amorphous alloy material comprises: 75 to 85 atomic% of Al; 5 to 10 atomic% of at least one element selected from Ni and Co; 5 to 12 atomic% of at least one element selected from the elements
And at least one element selected from B and C with 0.
5 to 5 atomic%, at least 50% by volume.
% Of amorphous material.
と、Fe、CoおよびNiから選ばれる少なくとも１種の元素
と、Ｂとを配合してなる非晶質合金材料を用いることを
特徴とする連結部材。4. A connecting member for connecting members, wherein Si
And an amorphous alloy material obtained by mixing B with at least one element selected from Fe, Co and Ni, and B.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP21097789A JP2777416B2 (en) | 1989-08-15 | 1989-08-15 | Connecting member |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP21097789A JP2777416B2 (en) | 1989-08-15 | 1989-08-15 | Connecting member |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH0375344A JPH0375344A (en) | 1991-03-29 |
| JP2777416B2 true JP2777416B2 (en) | 1998-07-16 |
Family
ID=16598264
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP21097789A Expired - Fee Related JP2777416B2 (en) | 1989-08-15 | 1989-08-15 | Connecting member |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP2777416B2 (en) |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP2726231A1 (en) * | 2011-07-01 | 2014-05-07 | Apple Inc. | Heat stake joining |
| KR20200034939A (en) * | 2018-09-24 | 2020-04-01 | 리퀴드메탈 테크놀로지스 인코포레이티드 | Amorphous metal rivet systems |
Families Citing this family (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2713470B2 (en) * | 1989-08-31 | 1998-02-16 | 健 増本 | Magnesium-based alloy foil or magnesium-based alloy fine wire and method for producing the same |
| JP2667258B2 (en) * | 1989-08-31 | 1997-10-27 | 健 増本 | Rare earth metal base alloy foil or rare earth metal base alloy fine wire and method for producing the same |
| JP2753739B2 (en) * | 1989-08-31 | 1998-05-20 | 健 増本 | Method for producing aluminum-based alloy foil or aluminum-based alloy fine wire |
| JP2639455B2 (en) * | 1990-03-09 | 1997-08-13 | 健 増本 | High strength amorphous alloy |
| WO2018064218A1 (en) | 2016-09-27 | 2018-04-05 | Novelis Inc. | Systems and methods for non-contact tensioning of a metal strip |
| CA3038298C (en) | 2016-09-27 | 2023-10-24 | Novelis Inc. | Rotating magnet heat induction |
-
1989
- 1989-08-15 JP JP21097789A patent/JP2777416B2/en not_active Expired - Fee Related
Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP2726231A1 (en) * | 2011-07-01 | 2014-05-07 | Apple Inc. | Heat stake joining |
| KR20200034939A (en) * | 2018-09-24 | 2020-04-01 | 리퀴드메탈 테크놀로지스 인코포레이티드 | Amorphous metal rivet systems |
| KR20220119352A (en) * | 2018-09-24 | 2022-08-29 | 리퀴드메탈 테크놀로지스 인코포레이티드 | Amorphous metal rivet systems |
| US11428257B2 (en) | 2018-09-24 | 2022-08-30 | Liquidmetal Technologies, Inc. | Amorphous metal rivet systems |
| KR102479384B1 (en) * | 2018-09-24 | 2022-12-21 | 리퀴드메탈 테크놀로지스 인코포레이티드 | Amorphous metal rivet systems |
| KR102520123B1 (en) * | 2018-09-24 | 2023-04-10 | 리퀴드메탈 테크놀로지스 인코포레이티드 | Amorphous metal rivet systems |
Also Published As
| Publication number | Publication date |
|---|---|
| JPH0375344A (en) | 1991-03-29 |
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