JPS62222039A - Aluminum alloy excellent in wear resistance and extrudability - Google Patents
Aluminum alloy excellent in wear resistance and extrudabilityInfo
- Publication number
- JPS62222039A JPS62222039A JP6534886A JP6534886A JPS62222039A JP S62222039 A JPS62222039 A JP S62222039A JP 6534886 A JP6534886 A JP 6534886A JP 6534886 A JP6534886 A JP 6534886A JP S62222039 A JPS62222039 A JP S62222039A
- Authority
- JP
- Japan
- Prior art keywords
- alloy
- wear resistance
- extrudability
- wear
- aluminum 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.)
- Granted
Links
- 229910000838 Al alloy Inorganic materials 0.000 title claims abstract description 16
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 13
- 239000000203 mixture Substances 0.000 claims abstract description 8
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 7
- 229910052725 zinc Inorganic materials 0.000 claims abstract description 7
- 239000012535 impurity Substances 0.000 claims abstract description 6
- 229910052726 zirconium Inorganic materials 0.000 claims abstract description 6
- 229910052782 aluminium Inorganic materials 0.000 claims abstract description 5
- 229910052720 vanadium Inorganic materials 0.000 claims abstract description 4
- 238000005266 casting Methods 0.000 abstract description 5
- 229910052742 iron Inorganic materials 0.000 abstract description 5
- 229910052802 copper Inorganic materials 0.000 abstract description 3
- 238000003754 machining Methods 0.000 abstract 1
- 229910045601 alloy Inorganic materials 0.000 description 44
- 239000000956 alloy Substances 0.000 description 44
- 238000001125 extrusion Methods 0.000 description 12
- 230000000052 comparative effect Effects 0.000 description 10
- 230000000694 effects Effects 0.000 description 9
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 9
- 229910000765 intermetallic Inorganic materials 0.000 description 7
- 150000001875 compounds Chemical class 0.000 description 6
- 238000005520 cutting process Methods 0.000 description 6
- 238000005260 corrosion Methods 0.000 description 5
- 230000007797 corrosion Effects 0.000 description 5
- 239000011856 silicon-based particle Substances 0.000 description 5
- 230000007423 decrease Effects 0.000 description 4
- 238000000265 homogenisation Methods 0.000 description 4
- 239000002245 particle Substances 0.000 description 4
- 229910019752 Mg2Si Inorganic materials 0.000 description 3
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 3
- 239000013078 crystal Substances 0.000 description 3
- 239000006104 solid solution Substances 0.000 description 3
- 229910019018 Mg 2 Si Inorganic materials 0.000 description 2
- 230000007547 defect Effects 0.000 description 2
- 229910052737 gold Inorganic materials 0.000 description 2
- 238000000034 method Methods 0.000 description 2
- 229910001018 Cast iron Inorganic materials 0.000 description 1
- 238000005299 abrasion Methods 0.000 description 1
- 238000005275 alloying Methods 0.000 description 1
- 230000033228 biological regulation Effects 0.000 description 1
- 230000002542 deteriorative effect Effects 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 230000005496 eutectics Effects 0.000 description 1
- 238000011156 evaluation Methods 0.000 description 1
- 235000012438 extruded product Nutrition 0.000 description 1
- 239000010931 gold Substances 0.000 description 1
- -1 gold metal compound Chemical class 0.000 description 1
- 230000001771 impaired effect Effects 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
- 229910052751 metal Inorganic materials 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 238000003825 pressing Methods 0.000 description 1
- 239000000243 solution Substances 0.000 description 1
- 230000003746 surface roughness Effects 0.000 description 1
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 1
Landscapes
- Extrusion Of Metal (AREA)
- Powder Metallurgy (AREA)
Abstract
Description
【発明の詳細な説明】
〔産業上の利用分野〕
この発明は耐摩耗性および押出性に丁ぐれたアルミニウ
ム合金に関するものである。DETAILED DESCRIPTION OF THE INVENTION [Field of Industrial Application] This invention relates to an aluminum alloy with excellent wear resistance and extrudability.
一般に、アルミニウムは硬度が低ぐて耐摩耗性に劣るの
で、その硬度を上げて耐摩耗性を向上させる友めに従東
種々の合金成分がアルミニウムに添加されており1例え
ば、JIS−H4140C規定される4032のアルミ
ニウム合金においては110〜13.Si量%という多
量のSi?添加して、アルミニウム中に硬質のS i
4′j子を分散させ。In general, aluminum has low hardness and poor wear resistance, so various alloying components are added to aluminum to increase its hardness and improve its wear resistance1.For example, JIS-H4140C regulations In the case of 4032 aluminum alloy, it is 110 to 13. A large amount of Si? Addition of hard Si into aluminum
4' Distribute the children.
それの耐摩耗性を冨めている。It has rich wear resistance.
しかしながら、上記の高Si含有アルミニウム合金は、
耐摩耗性にはすぐれているものの、押出性に劣るので、
特にポートホール押出によってパイプ等fr:装きする
のは回器であり、ま7’c S i粒子の硬変が非常に
高いところから、このようなアルミニウム合金の切削加
工に際しては、バイトの摩耗が激しく、さらに仕上面で
このSi粒子が脱落して切削面の粗度が低下し、概して
機械加工性にも劣る上に1M中に分散している多量のS
i粒子によって耐食性も損われるという問題があっ念。However, the above-mentioned high Si content aluminum alloy
Although it has excellent wear resistance, it has poor extrudability, so
Particularly, pipes, etc., are mounted by porthole extrusion using turning tools, and since the hardness of Si particles is extremely high, when cutting such aluminum alloys, wear of the cutting tool is a problem. In addition, these Si particles fall off on the finished surface, reducing the roughness of the cut surface, generally resulting in poor machinability, and a large amount of S dispersed in 1M.
Unfortunately, the i-particles also impair corrosion resistance.
本発明者等は、上述のような状況に鑑みて種々研究を重
ねた結果。The inventors of the present invention have conducted various studies in view of the above-mentioned circumstances.
(1) 前記高Si含有M合金中のSi含有量を1.
6〜4.9重量%と減らして、 Mg含有量を1.9〜
7.6重量%と増大させると、そのSi含有量の減少に
よってM合金の押出性と耐食性が向上するとともに。(1) The Si content in the high Si-containing M alloy is 1.
Reduce the Mg content to 6-4.9% by weight and reduce it to 1.9-4.9% by weight.
When the Si content is increased to 7.6% by weight, the extrudability and corrosion resistance of the M alloy are improved due to the decrease in Si content.
そのSiの大部分はiVIg 2S iなる金属間化合
物を形成し、このMg 2 S iがM中(二分散して
、前記Si含有量の減少に伴う耐摩耗性の低下を阻止す
ること、(2)前記のようなSiおよびMgを含むM合
金中にMnを0.5〜1.5重量%含有させると、この
Mnは後述のFeも含めてM −(Mn 、 Fe )
−3i系金金属化合物(α相)を形成し、このα相は
M中に分散してM@金の耐摩耗性を向上させること、
すなわち、前記(1)で述べたことと合わせると。Most of the Si forms an intermetallic compound called iVIg 2 Si, and this Mg 2 Si is bidispersed in M to prevent the decline in wear resistance associated with the decrease in Si content. 2) When 0.5 to 1.5% by weight of Mn is contained in the M alloy containing Si and Mg as described above, this Mn, including Fe (described later), becomes M - (Mn, Fe).
-3i-based gold metal compound (α phase) is formed, and this α phase is dispersed in M to improve the wear resistance of M@gold. In other words, in combination with what was stated in (1) above.
高Si含有M合金中に分散しているSi粒子の量を減ら
すことによって、このM合金の押出性と耐食性が向上し
、一方、その中でMgを増量し、かつMnを添加するこ
とによって、Mg2SiおよびM −(Mn 。By reducing the amount of Si particles dispersed in the high Si-containing M alloy, the extrudability and corrosion resistance of this M alloy are improved, while by increasing the amount of Mg and adding Mn therein, Mg2Si and M-(Mn.
Fe)−8i系化合物が形成し、これらの金属間化合物
はM中に分散して前記Si粒子の減少によって起る筈の
耐摩耗性の低下を補う結果、このように改変し念/V合
金は的記高81含有p、6 @gに匹敵する耐摩耗性を
保持しなから押出性にもすぐれたものとなること。Fe)-8i-based compounds are formed, and these intermetallic compounds are dispersed in M to compensate for the decrease in wear resistance that would occur due to the reduction of Si particles. It maintains abrasion resistance comparable to that of P, 6@g containing a target height of 81, and also has excellent extrudability.
(3) 上記のような量のSi昌句およびMnk含む
M合金中に、さらニFc : 0.3〜1.0%、Cr
:0.03〜025%、 Zr:0.05〜0.25%
およびV:0.03〜0.25%(%は丁べて重量%、
以下も特(=ことわらなければ%はすべて重量%を意味
する)のうちの1種または2種以上を添加すると、これ
らの成分は、前記Mnと同様に1AlおよびSiと結合
して前記AA −(Mn、 Fe ) Si系金属間
化合物2形成し、これらの化合物はM中に分散して、上
記M合金の耐摩耗性を一層向上させること。(3) In the M alloy containing the above amounts of Si and Mnk, further Fc: 0.3 to 1.0%, Cr
:0.03~025%, Zr:0.05~0.25%
and V: 0.03-0.25% (% is total weight%,
When one or more of the following are also added (=% means weight % unless otherwise specified), these components combine with 1Al and Si in the same manner as the above Mn to form the AA. - (Mn, Fe) Si-based intermetallic compounds 2 are formed and these compounds are dispersed in M to further improve the wear resistance of the M alloy.
(4) 前記量のSi、MgおよびMnをきむM合金
、またはこれにさらに前記量のFe 、 Cr 、 Z
rおよびVのうちの1種または2挿B上を含有させfc
M合金に。(4) M alloy containing the above amounts of Si, Mg and Mn, or further containing the above amounts of Fe, Cr, Z
fc containing one or two of r and V
For M alloy.
Cu:0.05〜0.5%およびZn:0.25〜1.
5%のうちの1種または2秤を添加すると、これらのM
合金の強度を高めること。Cu: 0.05-0.5% and Zn: 0.25-1.
The addition of one or two of these M
To increase the strength of the alloy.
を見出した。I found out.
この発明は、上記知見に基づいて発明されたもので、耐
摩耗性と押出性にすぐれ、かつ切削加工時にバイトの摩
耗や硬質粒子の脱落が少ないアルミニウム合金を提供す
ることを目的とし。This invention was invented based on the above knowledge, and aims to provide an aluminum alloy that has excellent wear resistance and extrudability, and is less likely to wear out the cutting tool or shed hard particles during cutting.
Mg:1.9〜7,6%。Mg: 1.9-7.6%.
Si:1.6〜4.9%、 Mn : 0.5〜1.5%。Si: 1.6-4.9%, Mn: 0.5-1.5%.
を含有し、さらに、必要に応じて Fe:0.3〜1.0%。and, if necessary, Fe: 0.3-1.0%.
Cr : 0.03〜0.25%1 Zr: 0.05〜0.25%。Cr: 0.03~0.25%1 Zr: 0.05-0.25%.
V:0.03〜0.25%。V: 0.03-0.25%.
のうちの1種または2種以上、および Cu: 0.05〜0.5%。one or more of the following, and Cu: 0.05-0.5%.
Zn: 0.25〜1.5%、
のうちの1種または2種を含有し、そして残りがAlお
よび不可避不純物からなる成分組成を有することを特徴
とする。耐摩耗性および押出性にすぐれtアルミニウム
合金。Zn: 0.25 to 1.5%, containing one or two of the following, and the remainder being Al and inevitable impurities. Aluminum alloy with excellent wear resistance and extrudability.
に係わるものである。This is related to.
つぎに、この発明において成分組成範囲を上記のとおり
に限定した理由を述べる。Next, the reason for limiting the component composition range as described above in this invention will be described.
(1) Mg
Mg成分には1M中に固溶してM合金の強度を高め、も
ってM合金の押出時における変形抵抗を大きくする作用
があるが、Siと共存することによりその大部分はMg
2 S sなる金属間化合物を形成するため、その押
出性を害うことかなく、このtVIg 2S iはM合
金の耐摩耗性の向上に寄与するっ
この発明のM合金においては、それに含有させルMg量
を1.9〜7.6%としているので、後述のSi含有量
:1.6〜4.9%と合わせると、 Mg2Si量とし
ては3〜12%となり、若干の過剰SiがMg 2S
i以外の形で含まれることになる。 この’Wig 2
S J含有量が3%未満では十分な耐摩耗性を得るこ
とができず、一方それが12%を越えると、初晶の形で
Mg 2 S iが晶出し、これがM合金の押出性や切
削性を害うことから、 Mg含有量は、このMg 2
S i含有量:3〜12%に対応する上記の1.9〜7
.6%に定めた。(1) Mg The Mg component has the effect of increasing the strength of the M alloy by solid solution in 1M, thereby increasing the deformation resistance during extrusion of the M alloy, but by coexisting with Si, most of the Mg component is dissolved in Mg.
Since it forms an intermetallic compound called 2Ss, this tVIg2Si contributes to improving the wear resistance of the M alloy without impairing its extrudability. Since the amount of Mg is 1.9 to 7.6%, when combined with the Si content (1.6 to 4.9%, which will be described later), the amount of Mg2Si is 3 to 12%. 2S
It will be included in a form other than i. This 'Wig 2
If the S J content is less than 3%, sufficient wear resistance cannot be obtained, while if it exceeds 12%, Mg 2 Si crystallizes in the form of primary crystals, which deteriorates the extrudability of the M alloy. Since it impairs machinability, the Mg content is
Si content: 1.9-7 above corresponding to 3-12%
.. It was set at 6%.
(2) 5i
Si532分は、上述のようにMgと結合してMg2S
iなる金属間化合物を形成し、このMg 281粒子は
M合金に耐摩耗性を付与するとともに、遊離のSi粒子
のようにM合金の耐食性を損うことがなく、またこのよ
うなMg 2S iを形成した上でさらに余ったSi成
分はM 、 Mn 、 6るいはさらに後述のFe +
Cr + Zr +■のうちのいずれか1種以上と結
合して1例えばA−e (Mn 、Fe ) S
i系の金属間化合物(α相)を形成し、このα相もM中
に分散して合金の耐摩耗を生2向上させる。(2) 5i Si532 is combined with Mg to form Mg2S as described above.
The Mg 281 particles form an intermetallic compound called i, and these Mg 281 particles impart wear resistance to the M alloy and do not impair the corrosion resistance of the M alloy like free Si particles. After forming, the remaining Si component is M, Mn, 6, or Fe + as described below.
Combined with any one or more of Cr + Zr + 1, for example, A-e (Mn, Fe) S
An i-based intermetallic compound (α phase) is formed, and this α phase is also dispersed in M to improve the wear resistance of the alloy.
したがって1Mgの項で述べた一2Si量と、このα相
を形成させるのに必要なSi量、さらに遊離のSi粒子
を形成させないSi量を考慮して、この発明ではSi含
有量を1,6〜4.9%と定めた。Therefore, in this invention, the Si content is set to 1,6 It was set at ~4.9%.
(31Mn
Mn暇分は、上述のように1AlおよびSiと結合して
、耐摩耗性の向上に寄与するα相の形成に役立つ成分で
あるが、その含有量が0.5%未満では耐摩耗性の向上
に効果がなく、またそれが1,5%を越えると、巨大な
初晶化合物を形成してM合金の切削性や伸び等に悪影響
を及ぼすことから、その含有量を0.5〜1.5%と定
めた。(31Mn Mn is a component that combines with 1Al and Si as described above and helps form the α phase that contributes to improving wear resistance, but if its content is less than 0.5%, wear resistance If it exceeds 1.5%, it will form a huge primary crystal compound and have a negative effect on the machinability and elongation of the M alloy, so the content should be reduced to 0.5%. It was set at ~1.5%.
(4) Fc 、 Cr 、 ZrおよびVFe 、
Cr 、 ZrおよびV成分は、いずれもMnと同様
taUおよびStと結合して金属間化合物な形成し。(4) Fc, Cr, Zr and VFe,
Like Mn, Cr, Zr, and V components all combine with taU and St to form intermetallic compounds.
もってA4合金の耐摩耗性を一層向上させる作用がある
ので、必要(:応じて添加されるが、その含有量がそれ
ぞれ0.3 、0.03 、0.05および0.03%
未満では前記耐摩耗性を一層向上させる作用が得られず
、一方それが、 Feについて1.0%pcrrZr、
Vについて0.25%をそれぞれ越えると、いずれも巨
大な初晶化合物を形成して合金の切削性と伸びを悪化さ
せることから、これら成分の含有量を、それぞれFeに
ついては0.3〜1.0%、Crおよび■について0.
03〜0.25%、モしてZrについては0.05〜0
.25%と定めた。This has the effect of further improving the wear resistance of A4 alloy, so it is necessary (: added as required, but the content is 0.3%, 0.03%, 0.05%, and 0.03%, respectively).
If it is less than 1.0% pcrrZr for Fe, the effect of further improving the wear resistance cannot be obtained;
If V exceeds 0.25%, giant primary crystal compounds are formed and the machinability and elongation of the alloy deteriorate. .0%, 0.0% for Cr and ■.
03-0.25%, and 0.05-0 for Zr
.. It was set at 25%.
(5) CuおよびZn
CuおよびZn成分は1MM中=固溶してその強度を高
める作用があるので、必要に応じてこの発明の合金中に
含有されるが、これらの含有量がCuで0.05%未満
、Zrで0.25%未満になると上記作用に十分な効果
が得られず、一方それが、Cuについて05%を越える
とM合金の耐食性が損われ。(5) Cu and Zn Cu and Zn components are dissolved in 1 MM = solid solution and have the effect of increasing its strength, so they are contained in the alloy of this invention as necessary, but if their content is 0 in Cu If it is less than 0.05% for Zr, and less than 0.25% for Zr, sufficient effects will not be obtained for the above-mentioned effects, while on the other hand, if it exceeds 0.5% for Cu, the corrosion resistance of the M alloy will be impaired.
モしてZnについて1.5%を越えると、切削時にその
M合金の表面仕上り性が悪化することから、これら成分
の含有量を、それぞれCuについては0.05〜0.5
%、モしてZnについては0.25〜1.5%と定めた
。However, if Zn exceeds 1.5%, the surface finish of the M alloy will deteriorate during cutting, so the content of these components should be adjusted to 0.05 to 0.5% for Cu.
%, and Zn was set at 0.25 to 1.5%.
なお、この発明のM合金においては、それの鋳造後に、
鋳造組織の均質化、Mg、Si成分等の固溶。In addition, in the M alloy of this invention, after casting it,
Homogenization of casting structure, solid solution of Mg, Si components, etc.
Mg2Si化合物の球状化およびM (Mn 、 F
e ) −8i系化合物の微細な析出を促進して、この
M合金に所望の耐摩耗性、押出性および強変を確実に付
与するためには均質化処理を施す必要があり、この均質
化処理の温度が400℃未満では前記効果が十分に得ら
れず、一方それが575℃を越えると部分的な共晶融解
を生ずる虞れがあることから、この温度は一般に400
〜575℃でなければならない。Spheroidization of Mg2Si compounds and M (Mn, F
e) In order to promote the fine precipitation of -8i-based compounds and reliably impart the desired wear resistance, extrudability and strong deformation to this M alloy, it is necessary to perform homogenization treatment, and this homogenization If the treatment temperature is less than 400°C, the above effect cannot be sufficiently obtained, while if it exceeds 575°C, there is a risk of partial eutectic melting.
Must be ~575°C.
また、この発明のM合金を押出しによって種々の部材に
加工する場合、この押出加工を350〜550°C以外
の己変で実施すると、押出時に表面クラックが発生し、
モして押出加工変が75%未満であると、鋳塊中の巣、
ピンホールなどの鋳造欠陥の上着が十分に達成されない
ために、これらの欠陥が押出後に残留して、製品の機械
的性質や切削加工後における表面性状が劣化するので、
この押出加工は350〜550℃の温度および75%以
上の押出加工変にお′いて遂行する必要がある。Furthermore, when the M alloy of the present invention is processed into various parts by extrusion, if the extrusion process is carried out at a temperature other than 350 to 550°C, surface cracks will occur during extrusion.
If the deformation during extrusion is less than 75%, cavities in the ingot,
Due to insufficient coverage of casting defects such as pinholes, these defects remain after extrusion, deteriorating the mechanical properties of the product and the surface quality after cutting.
This extrusion process must be carried out at a temperature of 350 DEG to 550 DEG C. and an extrusion change of greater than 75%.
ついで、比較例と対比しながら、この発明を実施例によ
って説明する。Next, the present invention will be explained by way of examples while comparing with comparative examples.
それぞれ第1表に示される成分組成を有する本発明M8
−金1〜13.この発明の範囲から外れた組成を有する
比較M合金1〜8(外れた成分を第1表中※印で示す)
、および前記JIS 4032の高Si含有M合金に
相当する従来M合金の溶湯から、いずれも直径=200
WrIrIのビレットを鋳造した後、これらのビレット
に、 温KI : 56 o℃ニ6時間保持の均質化処
理?施し、ついで湿質:500℃において各ビレットを
直径:36■の丸棒に押出した。 つぎに、これらの丸
棒を引張矯正した後、温度:530℃に1時間保持して
溶体化し、ついで水焼入れしてから、温v:tso’c
に8時間保持するT6処理を施した。The present invention M8 each having the component composition shown in Table 1.
- Fri 1-13. Comparative M alloys 1 to 8 having compositions outside the scope of this invention (deviating components are indicated by * in Table 1)
, and from the molten metal of the conventional M alloy corresponding to the high Si-containing M alloy of JIS 4032, both diameter = 200
After casting the WrIrI billets, these billets were subjected to a homogenization treatment at 56 o C for 6 hours. The billet was then extruded into a round bar with a diameter of 36 mm at a wet temperature of 500°C. Next, after tensile straightening these round bars, they were kept at a temperature of 530°C for 1 hour for solution treatment, then water quenched, and then heated to a temperature of 530°C.
was subjected to T6 treatment for 8 hours.
上記の押出時において、押出製品の表面に割れを生じさ
せないで丸棒を押出すことができる最大押出連間を測定
し、これによって前記各合金の押出性を評価した。During the above extrusion, the maximum extrusion length at which a round bar could be extruded without causing cracks on the surface of the extruded product was measured, and the extrudability of each of the alloys was evaluated based on this.
また、前記本発明1見合金、比taU合金および従来M
合金の耐摩耗性を評価するために、これらの合金からな
る前記各丸棒から、試験片として、接触面において4閣
の直径を有する円柱状のピンを切り出し、これらのピン
を、ピン・ディスク タイプの摩耗試験機な用い、接触
圧カニ3ooy/−1摩擦速M : l 250 m
/ mixの条件で回転しつつある相手材のFC25鋳
鉄製デイスクに100分間押しつけて各ピンの摩耗量を
測定した。In addition, the above-mentioned present invention first alloy, comparative taU alloy and conventional M
In order to evaluate the wear resistance of the alloys, cylindrical pins having a diameter of 4 mm at the contact surface were cut out as test pieces from each of the above-mentioned round bars made of these alloys, and these pins were divided into pin disks. Using a type of wear tester, contact pressure crab 3ooy/-1 friction speed M: l 250 m
The amount of wear on each pin was measured by pressing it against a rotating FC25 cast iron disk for 100 minutes under the conditions of /mix.
さらに、従来のJIS 4032合伯と比較した上記
M合eのバイト摩耗をそれぞれ観察して。Furthermore, we observed the tool wear of the above-mentioned M Goe compared to the conventional JIS 4032 Go Haku.
各バイトがこのJIS 4032合金の場合と同程変
の著しい摩耗を起して通常の表面粗IWを維持できなく
なったものをX印、この摩耗よりは軽変である若干の摩
耗を生じ友ものをΔ印、そして殆ど摩耗を生じなかった
ものをO印で評価した。Each tool is marked with an X if it has experienced significant wear similar to that of this JIS 4032 alloy and is no longer able to maintain the normal surface roughness IW. The evaluation was made with the mark Δ, and the case with almost no wear was evaluated with the mark O.
これらの結果も合わせて第1段に示した。These results are also shown in the first column.
第1表に示された結果から1本発明M合金1〜13では
いずれも最大押出速すが大きい上に摩耗量が少なく、か
つバイト摩耗も少ないのに対して。From the results shown in Table 1, the M alloys 1 to 13 of the present invention all have a high maximum extrusion speed, have a small amount of wear, and have little tool wear.
比較AJ@mlではMgとStが少な過ぎるために摩耗
量が多く、比較M合金2ではSiが十分存在していても
Mg量が少な過ぎるのでやはり耐摩耗性に劣り。Comparative AJ@ml has too little Mg and St, so the amount of wear is large, and Comparative M alloy 2 has too little Mg even though Si is present, so the wear resistance is still poor.
比較Ae合位3では嵐が多過ぎるために押出性が劣る上
にバイト摩耗が著しく、比較M合金4ではSt量が少な
すぎるために摩耗量が多く、比$!2AJ合金5では5
itJが多過ぎるためにバイト摩耗が激しく。Comparative Ae alignment 3 has too many storms, resulting in poor extrudability and significant bite wear. Comparative M alloy 4 has too little St content, resulting in a large amount of wear, and the ratio is $! 2AJ alloy 5 is 5
Too much itJ causes severe tool wear.
比較M合金6ではMgとSiが多過ぎるために押出性が
著しく悪い上にバイト摩耗が激しく、比較M合金7では
Mnが不足しているために耐摩耗性が低く、そして比較
M合金8ではMnが多過ぎるためにバイト摩耗が激しい
ことがわかる。Comparative M alloy 6 has too much Mg and Si, resulting in extremely poor extrudability and severe bite wear; comparative M alloy 7 has low wear resistance due to a lack of Mn; and comparative M alloy 8 has low wear resistance. It can be seen that tool wear is severe due to too much Mn.
吸上述べた説明から明らかなように、この発明によると
、すぐれた押出性ばかりでなく、従来の高Si含有層合
金に匹敵するか、またはそれ以上のすぐれた耐摩耗性も
そなえ、したがってこのような特性が特に要求される空
圧シリンダや油圧シリンダ等の摺動部品の素材として適
したM合金を提供することができる。As is clear from the above description, the present invention provides not only superior extrudability but also superior wear resistance, comparable to or better than conventional high Si-containing layer alloys; It is possible to provide an M alloy suitable as a material for sliding parts such as pneumatic cylinders and hydraulic cylinders that particularly require such properties.
Claims (4)
る成分組成(以上重量%)を有することを特徴とする、
耐摩耗性および押出性にすぐれたアルミニウム合金。(1) A component containing Mg: 1.9 to 7.6%, Si: 1.6 to 4.9%, Mn: 0.5 to 1.5%, and the remainder consisting of Al and inevitable impurities. characterized by having a composition (more than % by weight),
Aluminum alloy with excellent wear resistance and extrudability.
lおよび不可避不純物からなる成分組成(以上重量%)
を有することを特徴とする、耐摩耗性および押出性にす
ぐれたアルミニウム合金。(2) Contains Mg: 1.9 to 7.6%, Si: 1.6 to 4.9%, Mn: 0.5 to 1.5%, and further Fe: 0.3 to 1.0 %, Cr: 0.03-0.25%, Zr: 0.05-0.25%, V: 0.03-0.25%, and the remainder is A
Component composition consisting of l and unavoidable impurities (weight%)
An aluminum alloy with excellent wear resistance and extrudability.
よび不可避不純物からなる成分組成(以上重量%)を有
することを特徴とする、耐摩耗性および押出性にすぐれ
たアルミニウム合金。(3) Contains Mg: 1.9 to 7.6%, Si: 1.6 to 4.9%, Mn: 0.5 to 1.5%, and further Cu: 0.05 to 0.5. %, Zn: 0.25 to 1.5%, and the remainder is Al and inevitable impurities (weight %). Aluminum alloy with excellent wear resistance and extrudability.
よび不可避不純物からなる成分組成(以上重量%)を有
することを特徴とする、耐摩耗性および押出性にすぐれ
たアルミニウム合金。(4) Contains Mg: 1.9 to 7.6%, Si: 1.6 to 4.9%, Mn: 0.5 to 1.5%, and further Fe: 0.3 to 1.0 %, Cr: 0.03-0.25%, Zr: 0.05-0.25%, V: 0.03-0.25%, one or more of the following, and Cu: 0. Zn: 0.25 to 0.5%, Zn: 0.25 to 1.5%, and one or two of the following, and the remainder is Al and inevitable impurities (weight %). An aluminum alloy with excellent wear resistance and extrudability.
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP6534886A JPS62222039A (en) | 1986-03-24 | 1986-03-24 | Aluminum alloy excellent in wear resistance and extrudability |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP6534886A JPS62222039A (en) | 1986-03-24 | 1986-03-24 | Aluminum alloy excellent in wear resistance and extrudability |
Publications (2)
Publication Number | Publication Date |
---|---|
JPS62222039A true JPS62222039A (en) | 1987-09-30 |
JPH0557346B2 JPH0557346B2 (en) | 1993-08-23 |
Family
ID=13284356
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
JP6534886A Granted JPS62222039A (en) | 1986-03-24 | 1986-03-24 | Aluminum alloy excellent in wear resistance and extrudability |
Country Status (1)
Country | Link |
---|---|
JP (1) | JPS62222039A (en) |
Cited By (5)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US5110545A (en) * | 1989-02-24 | 1992-05-05 | Golden Aluminum Company | Aluminum alloy composition |
WO2010114063A1 (en) * | 2009-03-31 | 2010-10-07 | 日立金属株式会社 | Al-mg-si-type aluminum alloy for casting which has excellent bearing force, and casted member comprising same |
CN110184512A (en) * | 2019-07-15 | 2019-08-30 | 中南大学 | A kind of selective laser fusing Al alloy powder and its method for preparing eutectic reinforced aluminium alloy |
CN111809086A (en) * | 2019-04-12 | 2020-10-23 | 比亚迪股份有限公司 | Die-casting aluminum alloy and preparation method and application thereof |
CN114592148A (en) * | 2022-03-11 | 2022-06-07 | 中南大学 | High-strength and high-toughness Al-Mg for additive manufacturing2Si-Zn alloy and preparation method and application thereof |
-
1986
- 1986-03-24 JP JP6534886A patent/JPS62222039A/en active Granted
Cited By (7)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US5110545A (en) * | 1989-02-24 | 1992-05-05 | Golden Aluminum Company | Aluminum alloy composition |
WO2010114063A1 (en) * | 2009-03-31 | 2010-10-07 | 日立金属株式会社 | Al-mg-si-type aluminum alloy for casting which has excellent bearing force, and casted member comprising same |
US9518312B2 (en) | 2009-03-31 | 2016-12-13 | Hitachi Metals, Ltd. | Al—Mg—Si-based, casting aluminum alloy with excellent yield strength and cast member made thereof |
CN111809086A (en) * | 2019-04-12 | 2020-10-23 | 比亚迪股份有限公司 | Die-casting aluminum alloy and preparation method and application thereof |
CN111809086B (en) * | 2019-04-12 | 2021-12-07 | 比亚迪股份有限公司 | Die-casting aluminum alloy and preparation method and application thereof |
CN110184512A (en) * | 2019-07-15 | 2019-08-30 | 中南大学 | A kind of selective laser fusing Al alloy powder and its method for preparing eutectic reinforced aluminium alloy |
CN114592148A (en) * | 2022-03-11 | 2022-06-07 | 中南大学 | High-strength and high-toughness Al-Mg for additive manufacturing2Si-Zn alloy and preparation method and application thereof |
Also Published As
Publication number | Publication date |
---|---|
JPH0557346B2 (en) | 1993-08-23 |
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