JPS63307240A - High strength wear resistant al-si alloy forged member having low thermal expansion coefficient and its production - Google Patents
High strength wear resistant al-si alloy forged member having low thermal expansion coefficient and its productionInfo
- Publication number
- JPS63307240A JPS63307240A JP14122187A JP14122187A JPS63307240A JP S63307240 A JPS63307240 A JP S63307240A JP 14122187 A JP14122187 A JP 14122187A JP 14122187 A JP14122187 A JP 14122187A JP S63307240 A JPS63307240 A JP S63307240A
- Authority
- JP
- Japan
- Prior art keywords
- thermal expansion
- alloy powder
- alloy
- forged member
- green compact
- 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
- 229910021364 Al-Si alloy Inorganic materials 0.000 title claims abstract 6
- 238000004519 manufacturing process Methods 0.000 title claims description 6
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 23
- 239000000956 alloy Substances 0.000 claims abstract description 23
- 239000000843 powder Substances 0.000 claims abstract description 15
- 238000005242 forging Methods 0.000 claims abstract description 12
- 238000010438 heat treatment Methods 0.000 claims abstract description 9
- 229910000765 intermetallic Inorganic materials 0.000 claims abstract description 8
- 238000002844 melting Methods 0.000 claims abstract description 7
- 230000008018 melting Effects 0.000 claims abstract description 7
- 238000000034 method Methods 0.000 claims abstract description 7
- 229910052802 copper Inorganic materials 0.000 claims abstract description 6
- 239000012535 impurity Substances 0.000 claims abstract description 5
- 239000013078 crystal Substances 0.000 claims description 10
- 239000000203 mixture Substances 0.000 claims description 6
- 238000001816 cooling Methods 0.000 claims description 5
- 238000001556 precipitation Methods 0.000 claims description 5
- 238000005728 strengthening Methods 0.000 claims description 5
- 239000002245 particle Substances 0.000 claims description 4
- 239000000463 material Substances 0.000 claims description 3
- 229910018125 Al-Si Inorganic materials 0.000 claims 1
- 229910018520 Al—Si Inorganic materials 0.000 claims 1
- 229910000831 Steel Inorganic materials 0.000 claims 1
- 239000010959 steel Substances 0.000 claims 1
- 239000011159 matrix material Substances 0.000 abstract description 2
- 238000010791 quenching Methods 0.000 abstract 3
- 230000000171 quenching effect Effects 0.000 abstract 3
- 229910000838 Al alloy Inorganic materials 0.000 abstract 1
- 238000004881 precipitation hardening Methods 0.000 abstract 1
- 238000007493 shaping process Methods 0.000 abstract 1
- 229910013627 M-Si Inorganic materials 0.000 description 11
- 230000000694 effects Effects 0.000 description 6
- 238000012360 testing method Methods 0.000 description 5
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 3
- 229910000676 Si alloy Inorganic materials 0.000 description 3
- 238000005299 abrasion Methods 0.000 description 2
- 238000007796 conventional method Methods 0.000 description 2
- 229910052742 iron Inorganic materials 0.000 description 2
- 238000005259 measurement Methods 0.000 description 2
- 238000012545 processing Methods 0.000 description 2
- 238000007712 rapid solidification Methods 0.000 description 2
- 239000002994 raw material Substances 0.000 description 2
- 239000013585 weight reducing agent Substances 0.000 description 2
- 229910019752 Mg2Si Inorganic materials 0.000 description 1
- 238000000889 atomisation Methods 0.000 description 1
- 238000011109 contamination Methods 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 238000001125 extrusion Methods 0.000 description 1
- 238000001192 hot extrusion Methods 0.000 description 1
- 230000013011 mating Effects 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 150000002739 metals Chemical class 0.000 description 1
- 229910052759 nickel Inorganic materials 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 238000011160 research Methods 0.000 description 1
- 239000011863 silicon-based powder Substances 0.000 description 1
- 238000009864 tensile test Methods 0.000 description 1
- BPJYAXCTOHRFDQ-UHFFFAOYSA-L tetracopper;2,4,6-trioxido-1,3,5,2,4,6-trioxatriarsinane;diacetate Chemical compound [Cu+2].[Cu+2].[Cu+2].[Cu+2].CC([O-])=O.CC([O-])=O.[O-][As]1O[As]([O-])O[As]([O-])O1.[O-][As]1O[As]([O-])O[As]([O-])O1 BPJYAXCTOHRFDQ-UHFFFAOYSA-L 0.000 description 1
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 1
Landscapes
- Powder Metallurgy (AREA)
Abstract
Description
【発明の詳細な説明】
〔産業上の利用分野〕
この発明は、鉄の熱膨張係数（１２Ｘ １ ｏ−６／ｄ
ｅｇ）と同等の低い熱膨張係数（１４〜１２ Ｘ １０
／ｄｅｇ ）並びに高強度を有し、かつ耐摩耗性に
もすぐれ、特にこれらの特性が要求される各種のエンジ
ン部品やコンプレッサ部品などとして適用されるＭ−Ｓ
ｉ系合金鍛造部材およびその製造法に関するものである
。[Detailed Description of the Invention] [Industrial Application Field] This invention relates to the thermal expansion coefficient of iron (12X 1 o-6/d
Low coefficient of thermal expansion (14-12 x 10
/deg), high strength, and excellent wear resistance, and is used as various engine parts and compressor parts that especially require these characteristics.
The present invention relates to an i-based alloy forged member and a method for manufacturing the same.
従来、上記の各種部品の製造には、低熱膨張係数および
耐摩耗性が要求されることから、これらの特性を備えた
、Ｓｉ：３０〜５０重量％（以下、％は重量％を示す）
を含有し、さらに所要の合金成分を含有したＭ−Ｓｉ系
合金が用いられている。Conventionally, manufacturing of the various parts mentioned above requires a low coefficient of thermal expansion and wear resistance.
An M-Si alloy containing the following and further containing required alloy components is used.
これらの従来Ｍ−Ｓｉ系合金部材は、通常、原料粉末と
して、Ｓｉ扮末と、所定の組成を有するＭ合金粉末を用
い、これらを所定の割合に配合し、混合し、圧粉体に成
形した後、約３００〜５００℃の温度で熱間押出し加工
し、押出し加工後、直ちに急冷の溶体化処理を施すこと
によって製造されている。These conventional M-Si alloy members usually use Si powder and M alloy powder having a predetermined composition as raw material powders, and these are blended in a predetermined ratio, mixed, and formed into a green compact. After that, it is manufactured by hot extrusion processing at a temperature of about 300 to 500°C, and immediately after the extrusion processing, a rapid cooling solution treatment is performed.
しかし、近年、機関の葛性能化および軽量化に対する要
求が強まりつつあり、これに伴ってこれらの構造部材に
対する高強度化が強く望まれているが、上記の従来Ｍ−
Ｓｉ系合金押出部材は十分満足する高強度を具備しない
ために、これ（二対口することができないのが現状であ
る。However, in recent years, there has been a growing demand for improved engine performance and weight reduction, and along with this, there has been a strong desire for higher strength for these structural members.
Currently, Si-based alloy extruded members do not have a sufficiently high strength, so it is currently impossible to make them in two pairs.
そこで、本発明者等は、上述のような観点から、上記の
熱膨張係数が低く、かつすぐれた耐摩耗性を有するＳｉ
：３０〜５０％含有のＡｅ −Ｓｉ系合金に着目し、こ
れのもつすぐれた特性を損なうことなく、高強度化をは
かるべく研究を行なつこ結果、原料粉末として、
Ｓｉ：３０−５０％、 Ｃｕ：１〜５％、Ｍｇ：０
．５〜５％、
を含有し、残りがＡｌと不可避不純物からなる組成を有
する急冷凝固Ｍ−Ｓｉ系合金粉末を用い、これより圧粉
体を成形し、この圧粉体を、前記Ｍ −Ｓｉ系合金粉末
の融点直下、望ましくは４５０〜５２０℃の範囲内の温
度で熱間鍛造を施し、熱間鍛造後急冷して、高密度化と
初晶Ｓ１の微細化、並びに形状付与を行ない、引続いて
析出強化熱処理を施すこと（二よって製造されたＭ−Ｓ
ｉ系合金鍛造部材は、素地中（二、平均粒径：２〜１５
ｆｉｍの初晶Ｓｉと、同０．１μｍ以下の析出金属間化
合物が均一に分散した組織をもつよう（二なり、この熱
間鍛造（二より微細化した初晶Ｓｉと、析出強化熱処理
Ｃ二より析出した一段と微細な金属間化合物によって、
低熱膨張係数およびすぐれた耐摩耗性を具備した状態で
、高強度を有するようになるという知見を得たのである
。Therefore, from the above-mentioned viewpoints, the present inventors developed Si, which has a low coefficient of thermal expansion and excellent wear resistance.
We focused on Ae-Si alloys containing 30-50% Si and conducted research to increase their strength without sacrificing their excellent properties. Cu: 1-5%, Mg: 0
．． A green compact is formed from the rapidly solidified M-Si alloy powder having a composition of 5 to 5% of Hot forging is carried out at a temperature just below the melting point of the alloy powder, preferably within the range of 450 to 520°C, and after hot forging, it is rapidly cooled to increase the density, refine the primary crystal S1, and give it a shape, Subsequently, precipitation strengthening heat treatment is applied (the M-S produced by
The i-series alloy forged parts are made of
fim primary crystal Si and precipitated intermetallic compounds of 0.1 μm or less have a uniformly dispersed structure (2). Due to the finer intermetallic compounds precipitated,
They found that it has high strength while having a low coefficient of thermal expansion and excellent wear resistance.
この発明は、上記知見にもとづいてなされたものであっ
て、
Ｓｉ：３０〜５０％、 Ｃｕ：１〜５％、Ｍｇ ：
０．５〜５％、
を含有し、残りがＡｌと不可避不純物からなる組成、並
びに素地中に、平均粒径：２〜１５ｐｍの初晶Ｓｉと、
同０．１ ｐ ｍ以下の析出金属間化合物が均一に分散
した組織を有する低熱膨張係数を有する高強度耐摩耗性
Ｍ−Ｓｉ系合金鍛造部材、および、Ｓｉ：３０〜５０％
、 Ｃｕ：１〜５％、Ｍｇ：０．５〜５％、
を含有し、残りがＡｌと不可避不純物からなる組成を有
する急冷凝固１’Ｊ−Ｓｉ系合金粉末より成形した圧粉
体に、このＡｌ１−Ｓｉ系合金粉末の融点直下、望まし
くは４５０〜５２０℃の範囲内の温度で熱間鍛造を施し
、急冷して、高密度化と初晶Ｓｉの微細化、並びに形状
付与を行ない、引続いて析出強化熱処理を施すことによ
って、低熱膨張係数を有する高強度耐摩耗性Ｍ−Ｓｉ系
合金鍛造部材を製造する方法、
に特徴を有するものである。This invention was made based on the above findings, and includes: Si: 30-50%, Cu: 1-5%, Mg:
0.5 to 5%, with the remainder consisting of Al and unavoidable impurities, and primary crystal Si with an average grain size of 2 to 15 pm in the matrix,
A high-strength wear-resistant M-Si alloy forged member having a low thermal expansion coefficient and a structure in which precipitated intermetallic compounds of 0.1 pm or less are uniformly dispersed, and Si: 30 to 50%.
, Cu: 1 to 5%, Mg: 0.5 to 5%, and the remainder is Al and unavoidable impurities. Hot forging is performed at a temperature just below the melting point of this Al1-Si alloy powder, preferably within a range of 450 to 520 ° C., followed by rapid cooling to increase the density, refine the primary crystal Si, and give it a shape, The present invention is characterized by a method for manufacturing a high-strength, wear-resistant M-Si alloy forged member having a low coefficient of thermal expansion by subsequently performing precipitation strengthening heat treatment.
つぎに、この発明の鍛造部材および原料粉末の組成を上
記の通り（二限定した理由を説明する。Next, the reason why the compositions of the forged member and raw material powder of the present invention are limited to two as described above will be explained.
（ａｌ ５ｉ
Ｓｉ成分には、熱膨張係数を低め、かつ耐摩耗性を向上
させる作用があるが、その含有量が３０％未満では前記
作用に所望の効果が得られず、一方その含有量が５０％
を越えると熱間鍛造が困難となるこ、とから、その含有
量を３０〜５０％と定めた。(The al 5i Si component has the effect of lowering the coefficient of thermal expansion and improving wear resistance, but if its content is less than 30%, the desired effect cannot be obtained; 50%
Since hot forging becomes difficult if the content exceeds 30% to 50%.
なお、３６〜４５％の含有が望ましい。Note that the content is preferably 36 to 45%.
Φ） ＣｕおよびＭｇ
これらの成分には、いずれも熱処理時に素地中に微細な
Ｍｇ２Ｓｉ＋Ｃｕ２Ａｌなどの金属間化合物として析出
し、熱間鍛造により初晶Ｓｉが微細化されることと合ま
って、強度を著しく向上させる作用があるが、その含有
量がＣｕ ： １％未満およびＭｇ：０．５％未満では
前記作用に所望の効果が得られず、一方Ｃｕ ： ５％
およびＭｇ ： ５％を越えて含有させてもより一層の
向上効果は現われず、経済性を考慮して、その含有量を
Ｃｕ：１〜５％、Ｍｇ ： ０．５−５ ％と定めた。Φ) Cu and Mg Both of these components precipitate as fine intermetallic compounds such as Mg2Si+Cu2Al in the base material during heat treatment, and together with the refinement of primary crystal Si by hot forging, they increase strength. However, if the content of Cu is less than 1% and Mg is less than 0.5%, the desired effect cannot be obtained; on the other hand, Cu: 5%
And Mg: Even if the content exceeds 5%, no further improvement effect appears, so in consideration of economic efficiency, the content was determined to be Cu: 1 to 5% and Mg: 0.5 to 5%. .
なお、上記のように、この発明の鍛造部材においては、
初晶Ｓｉの平均粒径を２〜１５／Ｊｍとする必要がある
のであって、これはその平均粒径が２μｍ未満では、所
望の低熱膨張係数および耐摩耗性を確保することができ
ず、一方その平均粒径が１５μｍを越えると、強度、靭
性、および加工性が低下するようになるという理由によ
るものであり、かつこの平均粒径は熱間鍛造における温
度、加工率、および回数などによって自由に調製するこ
とができる。また、平均粒径：０．１１１ｍ以下の金属
間化合物は、熱間鍛造後急冷の溶体化処理についで、析
出強化熱処理を施すことによって、必然的に形成される
ものである。In addition, as mentioned above, in the forged member of this invention,
It is necessary to set the average grain size of primary Si to 2 to 15/Jm, because if the average grain size is less than 2 μm, the desired low coefficient of thermal expansion and wear resistance cannot be secured. On the other hand, if the average grain size exceeds 15 μm, strength, toughness, and workability will decrease, and this average grain size will vary depending on the temperature, working rate, number of times, etc. during hot forging. Can be prepared freely. Further, the intermetallic compound having an average grain size of 0.111 m or less is inevitably formed by performing precipitation strengthening heat treatment following hot forging and rapid cooling solution treatment.
さらに、この発明の鍛造部材は、溶解時のるつぼなどか
らの混入により、不可避不純物としてＦｅやＮｉなどの
成分を含有する場合があるが、その含有量が全体で２％
以下であれば、何ら影響を及ぼすものではないので、そ
の含有が許容される。Furthermore, the forged member of the present invention may contain components such as Fe and Ni as unavoidable impurities due to contamination from the crucible during melting, but the total content is 2%.
If it is below, it will not have any influence and its inclusion is permitted.
つぎに、この発明の鍛造部材およびその製造法を実施例
により具体的に説明する。Next, the forged member of the present invention and its manufacturing method will be specifically explained using examples.
通常のるつぼ炉を用い、各種のＭ合金溶湯を調製し、こ
れを空気アトマイズ法により１０２〜ｂ表に示される成
分組成、並びＣ−１００〜＋３５０ｍｅｓｈの粒度をも
ったＡｌ１−Ｓｉ系合金粉末を成形し、この急冷凝固Ｍ
−Ｓｉ系合金粉末より５ ｔｏｎ ／ ａｌの圧力で１
０ ｒｒａｎ Ｘ ２３ ｍｍ Ｘ ５５ ｍｍの寸法
をもった圧粉体を成形し、ついでこれらの圧粉体に対し
て、大気中、前記Ａ／！−Ｓｉ系合金粉末の融点直下の
温度である５００℃に６０分間加熱保持した後、３ ｔ
ｏｎ／ｄの荷重で一次熱間鍛造を施して、高密度化と初
晶Ｓｉの微細化をはかると共に、その寸法を１１ｒｔａ
ｎ Ｘ １６ ｒａｎ Ｘ ５７ ｍとし、引続いて再
び大気中、温度：５００℃に１５分間保持後、同じ＜
３１ｏｎ／ｃＩＨの荷重にて２次熱間鍛造を行なって、
１４聴Ｘ１２ｍｍＸ６０ｍｍの寸法に形状付与した後、
直ちに水冷の溶体化処理を施し、最終的に温度＝１７０
℃ｌ二６時間保持の析出強化熱処理を行なうことによっ
て本発明法１〜９を実施し、実質的に上記の急冷凝固Ｍ
−Ｓｉ系合金粉末と同一の成分組成をもった本発明鍛造
部材をそれぞれ製造した。Using an ordinary crucible furnace, prepare various M alloy molten metals, and use the air atomization method to produce Al1-Si alloy powders having the composition shown in Table 102-b and the particle size of C-100 to +350 mesh. This rapid solidification M
-1 at a pressure of 5 ton/al from Si-based alloy powder
Green compacts with dimensions of 0 rran x 23 mm x 55 mm are formed, and then these green compacts are subjected to the above-mentioned A/! in air. - After heating and holding for 60 minutes at 500°C, which is a temperature just below the melting point of Si-based alloy powder, 3 t
Primary hot forging was performed under a load of on/d to increase the density and refine the primary crystal Si, and the dimensions were reduced to 11rta.
n x 16 ran
Performing secondary hot forging under a load of 31 on/cIH,
After adding the shape to the dimensions of 14 mm x 12 mm x 60 mm,
Immediately subjected to water cooling solution treatment, finally temperature = 170
Methods 1 to 9 of the present invention are carried out by carrying out precipitation strengthening heat treatment held at ℃ 1 for 26 hours, and substantially the above-mentioned rapid solidification M
-Forged members of the present invention having the same composition as the Si-based alloy powder were manufactured.
ついで、この本発明鍛造部材について、金属顕微鏡によ
り初晶Ｓ１および金属間化合物の平均粒径を測定すると
共に、熱膨張係数を測定し、さらに引張試験および摩耗
試験を行なった。Next, regarding this forged member of the present invention, the average particle size of the primary crystal S1 and the intermetallic compound was measured using a metallurgical microscope, the coefficient of thermal expansion was measured, and a tensile test and an abrasion test were conducted.
なお、熱膨張係数は、直径＝５咽×長さ：１５請の試片
を用い、２０〜１５０℃間の値を測定し、また引張試験
には、平行部（二おける寸法が、直径：５１＋＋＋＋＋
×長さ：２０咽の試片を用い、さらに摩耗試験は、大越
式試験機を用い、相手材：Ｆｅ１２、最終荷重：２Ｋｇ
、摺動速度： ３．３ ｒｌ ／ｓｅｃ、摩耗距離：１
００ｍの条件で乾式で行ない、比摩耗量を測定した。こ
れらの測定結果を第１表に示した。The coefficient of thermal expansion was measured at a value between 20 and 150°C using a specimen with a diameter of 5 mm and a length of 15 mm; 51++++++
×Length: Using a 20mm test piece, further abrasion test was performed using an Okoshi type testing machine, mating material: Fe12, final load: 2Kg
, sliding speed: 3.3 rl/sec, wear distance: 1
The test was carried out in a dry manner under the conditions of 00 m, and the specific wear amount was measured. The results of these measurements are shown in Table 1.
また、第１表には、比較の目的で、従来法（二よって製
造されたＳｉ：４０．３％含有のＭ−Ｓｉ系合金押出部
材の同一条件での測定結果を示した。Furthermore, for the purpose of comparison, Table 1 shows the measurement results of an M-Si alloy extruded member containing 40.3% Si manufactured by the conventional method (2) under the same conditions.
第１表（１示される結果から、本発明法１〜９によって
製造された本発明鍛造部材は、いずれも従来法によって
製造されたＭ−Ｓｉ系合金押出部材に比して、初晶Ｓｉ
の平均粒径が細かく、したがって一段と高い強度を有し
、かつ前記Ｍ−Ｓｉ系合金押出部材と同等の低い熱膨張
係数およびすぐれた耐摩耗性を有することが明らかであ
る。From the results shown in Table 1 (1), it can be seen that the forged members of the present invention manufactured by methods 1 to 9 of the present invention have a higher primary crystal Si content than the M-Si alloy extruded members manufactured by the conventional method.
It is clear that the average particle size of the M-Si alloy extruded member is finer, and therefore has higher strength, as well as a low coefficient of thermal expansion and excellent wear resistance equivalent to the M-Si alloy extruded member.
上述のように、この発明の方法によれば、従来ＩＪ−Ｓ
ｉ系合金押出部材と同等の低熱膨張係数および耐摩耗性
を有し、これより一段とすぐれた強度を有するＭ−Ｓｉ
系合金鍛造部材を製造することができ、したがってこの
Ｍ−Ｓｉ系合金鍛造部材によれば、各種機関の高性能化
および軽量化に大いに寄与するなど工業上有用な効果が
もたらされるのである。As described above, according to the method of the present invention, conventional IJ-S
M-Si has a low coefficient of thermal expansion and wear resistance equivalent to that of i-based alloy extruded members, but has superior strength.
Therefore, this M-Si alloy forged member brings about industrially useful effects such as greatly contributing to higher performance and weight reduction of various engines.
Claims (2)
．５〜５％、 を含有し、残りがＡｌと不可避不純物からなる組成（以
上重量％）、並びに素地中に、平均粒径：２〜１５μｍ
の初晶Ｓｉと、同０．１μｍ以下の析出金属間化合物が
均一に分散した組織を有することを特徴とする低熱膨張
係数を有する高強度耐摩耗性Ａｌ−Ｓｉ系合金鍛造部材
。(1) Si: 30-50%, Cu: 1-5%, Mg: 0
．． 5 to 5%, with the remainder consisting of Al and unavoidable impurities (wt%), and an average particle size of 2 to 15 μm in the base material.
A high-strength, wear-resistant Al-Si based alloy forged member having a low coefficient of thermal expansion, characterized by having a structure in which primary crystal Si of 0.1 μm or less and precipitated intermetallic compounds of 0.1 μm or less are uniformly dispersed.
．５〜５％、 を含有し、残りがＡｌと不可避不純物からなる組成（以
上重量％）を有する急冷凝固Ａｌ−Ｓｉ系合金粉末より
成形した圧粉体に、このＡｌ−Ｓｉ系合金粉末の融点直
下の温度で熱間鍛造を施し、急冷して、高密度化と初晶
Ｓｉの微細化、並びに形状付与を行ない、引続いて析出
強化熱処理を施すことを特徴とする低熱膨張係数を有す
る高強度耐摩耗性Ａｌ−Ｓｉ系合金鍛造部材の製造法。(2) Si: 30-50%, Cu: 1-5%, Mg: 0
．． The melting point of this Al-Si alloy powder is molded into a green compact formed from a rapidly solidified Al-Si alloy powder having a composition (wt%) containing 5 to 5% of High-quality steel with a low coefficient of thermal expansion, which is characterized by hot forging at a temperature just below that, followed by rapid cooling to increase the density, refine the primary Si crystals, and give it a shape, followed by precipitation strengthening heat treatment. A method for manufacturing a strong and wear-resistant Al-Si alloy forged member.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP62141221A JP2856251B2 (en) | 1987-06-05 | 1987-06-05 | High-strength wear-resistant Al-Si alloy forged member having low coefficient of thermal expansion and method for producing the same |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP62141221A JP2856251B2 (en) | 1987-06-05 | 1987-06-05 | High-strength wear-resistant Al-Si alloy forged member having low coefficient of thermal expansion and method for producing the same |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS63307240A true JPS63307240A (en) | 1988-12-14 |
| JP2856251B2 JP2856251B2 (en) | 1999-02-10 |
Family
ID=15286942
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP62141221A Expired - Lifetime JP2856251B2 (en) | 1987-06-05 | 1987-06-05 | High-strength wear-resistant Al-Si alloy forged member having low coefficient of thermal expansion and method for producing the same |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP2856251B2 (en) |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH02185956A (en) * | 1989-01-12 | 1990-07-20 | Nissan Motor Co Ltd | Solution heat treatment for aluminum-type hot forged product |
| JPH0551683A (en) * | 1991-07-22 | 1993-03-02 | Toyo Alum Kk | Hypereutectic al-si powder metallurgical alloy with high strength |
| US10385622B2 (en) * | 2014-09-18 | 2019-08-20 | Halliburton Energy Services, Inc. | Precipitation hardened matrix drill bit |
Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5913041A (en) * | 1982-07-12 | 1984-01-23 | Showa Denko Kk | Aluminum alloy powder having high resistance to heat and abrasion and high strength and molding of said alloy powder and its production |
| JPS61238947A (en) * | 1985-04-16 | 1986-10-24 | Sumitomo Light Metal Ind Ltd | Manufacture of al-si alloy blank |
-
1987
- 1987-06-05 JP JP62141221A patent/JP2856251B2/en not_active Expired - Lifetime
Patent Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5913041A (en) * | 1982-07-12 | 1984-01-23 | Showa Denko Kk | Aluminum alloy powder having high resistance to heat and abrasion and high strength and molding of said alloy powder and its production |
| JPS61238947A (en) * | 1985-04-16 | 1986-10-24 | Sumitomo Light Metal Ind Ltd | Manufacture of al-si alloy blank |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH02185956A (en) * | 1989-01-12 | 1990-07-20 | Nissan Motor Co Ltd | Solution heat treatment for aluminum-type hot forged product |
| JPH0551683A (en) * | 1991-07-22 | 1993-03-02 | Toyo Alum Kk | Hypereutectic al-si powder metallurgical alloy with high strength |
| US10385622B2 (en) * | 2014-09-18 | 2019-08-20 | Halliburton Energy Services, Inc. | Precipitation hardened matrix drill bit |
Also Published As
| Publication number | Publication date |
|---|---|
| JP2856251B2 (en) | 1999-02-10 |
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