JP4956165B2 - Free-cutting aluminum alloy extruded material with excellent corrosion resistance to alcohol liquids containing OH groups - Google Patents
Free-cutting aluminum alloy extruded material with excellent corrosion resistance to alcohol liquids containing OH groups Download PDFInfo
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- JP4956165B2 JP4956165B2 JP2006331434A JP2006331434A JP4956165B2 JP 4956165 B2 JP4956165 B2 JP 4956165B2 JP 2006331434 A JP2006331434 A JP 2006331434A JP 2006331434 A JP2006331434 A JP 2006331434A JP 4956165 B2 JP4956165 B2 JP 4956165B2
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- LFQSCWFLJHTTHZ-UHFFFAOYSA-N Ethanol Chemical compound CCO LFQSCWFLJHTTHZ-UHFFFAOYSA-N 0.000 title claims description 37
- 238000005520 cutting process Methods 0.000 title claims description 32
- 230000007797 corrosion Effects 0.000 title claims description 31
- 238000005260 corrosion Methods 0.000 title claims description 31
- 229910000838 Al alloy Inorganic materials 0.000 title claims description 28
- 239000000463 material Substances 0.000 title claims description 23
- 125000002887 hydroxy group Chemical group [H]O* 0.000 title claims description 22
- 239000007788 liquid Substances 0.000 title claims description 8
- 229910052797 bismuth Inorganic materials 0.000 claims description 30
- 229910052718 tin Inorganic materials 0.000 claims description 29
- 239000012535 impurity Substances 0.000 claims description 12
- 229910052802 copper Inorganic materials 0.000 claims description 9
- 229910052742 iron Inorganic materials 0.000 claims description 5
- 239000000956 alloy Substances 0.000 description 43
- 229910045601 alloy Inorganic materials 0.000 description 42
- 239000000243 solution Substances 0.000 description 20
- 230000000052 comparative effect Effects 0.000 description 16
- 238000012360 testing method Methods 0.000 description 16
- 238000011156 evaluation Methods 0.000 description 14
- 238000004090 dissolution Methods 0.000 description 9
- 230000000694 effects Effects 0.000 description 8
- 238000002844 melting Methods 0.000 description 7
- 230000008018 melting Effects 0.000 description 7
- 238000007654 immersion Methods 0.000 description 6
- 229910021365 Al-Mg-Si alloy Inorganic materials 0.000 description 4
- 230000032683 aging Effects 0.000 description 4
- 150000001875 compounds Chemical class 0.000 description 4
- 238000007796 conventional method Methods 0.000 description 4
- 150000003839 salts Chemical class 0.000 description 4
- 239000007921 spray Substances 0.000 description 4
- 238000005496 tempering Methods 0.000 description 3
- 229910020830 Sn-Bi Inorganic materials 0.000 description 2
- 229910018728 Sn—Bi Inorganic materials 0.000 description 2
- 238000005266 casting Methods 0.000 description 2
- 239000013078 crystal Substances 0.000 description 2
- 230000003247 decreasing effect Effects 0.000 description 2
- 238000001125 extrusion Methods 0.000 description 2
- 239000012530 fluid Substances 0.000 description 2
- 238000001192 hot extrusion Methods 0.000 description 2
- 229910052745 lead Inorganic materials 0.000 description 2
- 238000004519 manufacturing process Methods 0.000 description 2
- 239000000203 mixture Substances 0.000 description 2
- 238000007670 refining Methods 0.000 description 2
- 238000005482 strain hardening Methods 0.000 description 2
- JLGLQAWTXXGVEM-UHFFFAOYSA-N triethylene glycol monomethyl ether Chemical compound COCCOCCOCCO JLGLQAWTXXGVEM-UHFFFAOYSA-N 0.000 description 2
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 2
- 230000004580 weight loss Effects 0.000 description 2
- 239000013585 weight reducing agent Substances 0.000 description 2
- 229910018084 Al-Fe Inorganic materials 0.000 description 1
- 229910018182 Al—Cu Inorganic materials 0.000 description 1
- 229910018192 Al—Fe Inorganic materials 0.000 description 1
- 229910018191 Al—Fe—Si Inorganic materials 0.000 description 1
- 229910018464 Al—Mg—Si Inorganic materials 0.000 description 1
- 101000825841 Homo sapiens Vacuolar-sorting protein SNF8 Proteins 0.000 description 1
- 229910019018 Mg 2 Si Inorganic materials 0.000 description 1
- 102100022787 Vacuolar-sorting protein SNF8 Human genes 0.000 description 1
- 230000002411 adverse Effects 0.000 description 1
- 150000001298 alcohols Chemical class 0.000 description 1
- 150000004703 alkoxides Chemical class 0.000 description 1
- 229910052782 aluminium Inorganic materials 0.000 description 1
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 1
- 239000000470 constituent Substances 0.000 description 1
- 230000007423 decrease Effects 0.000 description 1
- 238000007598 dipping method Methods 0.000 description 1
- 230000007613 environmental effect Effects 0.000 description 1
- 238000002474 experimental method Methods 0.000 description 1
- 238000000265 homogenisation Methods 0.000 description 1
- 238000003754 machining Methods 0.000 description 1
- 239000011159 matrix material Substances 0.000 description 1
- 239000000155 melt Substances 0.000 description 1
- 238000000034 method Methods 0.000 description 1
- 230000003287 optical effect Effects 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 238000012545 processing Methods 0.000 description 1
- 239000000047 product Substances 0.000 description 1
- 230000001105 regulatory effect Effects 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 230000035882 stress Effects 0.000 description 1
- 230000000007 visual effect Effects 0.000 description 1
Description
この発明は、切削性に優れた快削アルミニウム合金押出材、特にＰｂを添加することなく切削性を向上させた快削アルミニウム合金押出材に関するものであり、ＯＨ基を含むアルコール液に対する耐食性に優れた快削アルミニウム合金押出材を提供するものである。 The present invention relates to a free-cutting aluminum alloy extruded material excellent in machinability, in particular, a free-cutting aluminum alloy extruded material improved in machinability without adding Pb, and excellent in corrosion resistance to an alcohol liquid containing an OH group. A free-cutting aluminum alloy extruded material is provided.
周知のようにアルミニウム合金は一般に切削性が良好であるため、軸受け、光学部品、自動車部品など、切削加工が必要とされる部品、部材に従来から広く使用されている。このようなアルミニウム合金の切削加工においては、切粉が連続した長いものとならずに細かく分断されること、すなわち切粉分断性が良好であることが望ましいとされている。 As is well known, since aluminum alloys generally have good cutting properties, they have been widely used for parts and members that require cutting, such as bearings, optical parts, and automobile parts. In such an aluminum alloy cutting process, it is desirable that the chips are finely divided without being continuous and long, that is, it is preferable that the chips are good.
ところで従来、切削性に優れたアルミニウム合金材としては、Ａｌ−Ｃｕ合金に、Ｐｂ、Ｂｉを添加したＪＩＳ２０１１合金や、Ａｌ−Ｍｇ−Ｓｉ系合金にＰｂ、Ｂｉを添加したＪＩＳ６２６２合金などの押出材が多用されている。しかしながら、Ｐｂは環境に悪影響を及ぼすおそれがあるところから、近年は環境問題重視の観点から、Ｐｂを添加せずに切削性を向上させたアルミニウム合金が要求されるようになっている。そこで最近では、Ｐｂ−Ｂｉを添加したＪＩＳ６２６２合金（Ｐｂ−Ｂｉ添加）に代えて、Ｐｂを添加しないＳｎ−Ｂｉ添加合金が提案されており、切削性、耐食性などにおいてＪＩＳ６２６２合金とほぼ同等の性能を持つ快削アルミニウム合金が流通されつつある（例えば特許文献１参照）。
前記提案に示されるようなＳｎ−Ｂｉ添加快削アルミニウム合金においては、１２０℃以上の高温において、ＯＨ基を１つ以上含むアルコール液に接すれば腐食もしくは溶解するという現象が生じてしまう問題がある。この現象は、Ｓｎ添加合金に顕著に見られるものであり、高温で反応が著しく、またガスを発生しながら反応すること、さらに反応に潜伏期間が存在すること、そして特にＯＨ基が存在するアルコール液で溶解することなどが確認されており、これらの点から、アルコキシド反応によるものと推定されている。そのためＳｎ−Ｂｉ添加アルミニウム合金を、例えばブレーキ部品として使用して、ＯＨ基を１つ以上含む高温ブレーキ液と接触させた場合には、Ｓｎ−Ｂｉ添加アルミニウム合金が、腐食もしくは溶解してしまって、ブレーキ部品としての機能を果たさなくなることが懸念される。そのためＳｎ−Ｂｉ添加快削アルミニウム合金は、Ｐｂを添加せずに良好な切削性を確保できる利点はあるものの、ブレーキ部品など、高温のＯＨ基含有アルコール液と接するような環境での使用はためらわれていたのが実情である。 The Sn-Bi-added free-cutting aluminum alloy as shown in the above proposal has a problem that it causes corrosion or dissolution when it comes into contact with an alcohol solution containing one or more OH groups at a high temperature of 120 ° C or higher. . This phenomenon is prominently observed in Sn-added alloys. The reaction is remarkable at high temperatures, the reaction occurs while gas is generated, and there is a latent period in the reaction. It has been confirmed that it is dissolved in a liquid, and from these points, it is presumed to be due to an alkoxide reaction. Therefore, when the Sn—Bi-added aluminum alloy is used as a brake component, for example, and brought into contact with a high-temperature brake fluid containing one or more OH groups, the Sn—Bi-added aluminum alloy is corroded or dissolved. There is a concern that it will no longer function as a brake component. Therefore, although the Sn-Bi-added free-cutting aluminum alloy has the advantage of ensuring good machinability without adding Pb, its use in an environment where it comes into contact with a high-temperature OH group-containing alcohol solution such as brake parts is reluctant. It was the actual situation.
この発明は以上の事情を背景としてなされたもので、Ａｌ−Ｍｇ−Ｓｉ系合金において、Ｐｂを添加せずにＳｎおよびＢｉを添加して良好な切削性を維持すると同時に、ＯＨ基を１つ以上含む高温アルコール液との腐食反応を抑制し得る快削アルミニウム合金押出材を提供することを課題とするものである。 The present invention was made against the background described above. In an Al—Mg—Si alloy, Sn and Bi were added without adding Pb to maintain good machinability, and at the same time, one OH group was added. It is an object of the present invention to provide a free-cutting aluminum alloy extruded material that can suppress the corrosion reaction with the high-temperature alcohol solution contained above.
本発明者等は、前述の課題を解決するべく、鋭意実験・検討を重ねた結果、Ｐｂを添加しないＡｌ−Ｍｇ−Ｓｉ系合金において、Ｓｎ、Ｂｉを添加しつつも、Ｓｎ添加量を適切に規制すると同時に、新たにＣｕを適切な量だけ添加することによって、良好な切削性を確保しつつ、ＯＨ基を含有する高温アルコール液との接触による腐食、溶解を抑制し得ることを見出し、この発明をなすに至ったのである。 As a result of intensive experiments and examinations to solve the above-mentioned problems, the present inventors have found that an appropriate amount of Sn is added while adding Sn and Bi in an Al-Mg-Si alloy not containing Pb. At the same time, by adding an appropriate amount of Cu newly, it was found that corrosion and dissolution due to contact with a high-temperature alcohol solution containing OH groups can be suppressed while ensuring good cutting properties, It came to make this invention.
すなわち請求項１の快削アルミニウム合金押出材は、Ｓｉ０．４〜０．８％、Ｃｕ０．１〜０．４％、Ｍｇ０．８〜１．２％、Ｓｎ０．１〜０．５％、Ｂｉ０．３〜１．０％を含有し、かつＳｎとＢｉの合計量が０．５〜１．５％の範囲内にあり、残部がＡｌおよび不可避的不純物よりなることを特徴とするものである。 That is, the free-cutting aluminum alloy extruded material of claim 1 has Si 0.4 to 0.8%, Cu 0.1 to 0.4%, Mg 0.8 to 1.2%, Sn 0.1 to 0.5%, Bi0. 0.3 to 1.0%, and the total amount of Sn and Bi is in the range of 0.5 to 1.5%, and the balance is made of Al and inevitable impurities. .
また請求項２の発明の快削アルミニウム合金押出材は、Ｓｉ０．４〜０．８％、Ｃｕ０．１〜０．４％、Ｍｇ０．８〜１．２％、Ｓｎ０．１〜０．５％、Ｂｉ０．３〜１．０％、Ｆｅ０．７５〜０．９％を含有し、かつＳｎとＢｉの合計量が０．５〜１．５％の範囲内にあり、残部がＡｌおよび不可避的不純物よりなることを特徴とするものである。 Further, the free-cutting aluminum alloy extruded material of the invention of claim 2 is Si 0.4 to 0.8%, Cu 0.1 to 0.4%, Mg 0.8 to 1.2%, Sn 0.1 to 0.5%. , Bi 0.3-1.0%, Fe 0.75-0.9%, and the total amount of Sn and Bi is in the range of 0.5-1.5%, the balance being Al and inevitable It consists of impurities.
そしてまた請求項３の発明の快削アルミニウム合金押出材は、Ｓｉ０．４〜０．８％、Ｃｕ０．１〜０．４％、Ｍｇ０．８〜１．２％、Ｓｎ０．１〜０．５％、Ｂｉ０．３〜１．０％、Ｔｉ０．０１〜０．２０％を含有し、かつＳｎとＢｉの合計量が０．５〜１．５％の範囲内にあり、残部がＡｌおよび不可避的不純物よりなることを特徴とするものである。 Further, the free-cutting aluminum alloy extruded material of the invention of claim 3 is Si 0.4 to 0.8%, Cu 0.1 to 0.4%, Mg 0.8 to 1.2%, Sn 0.1 to 0.5. %, Bi 0.3 to 1.0%, Ti 0.01 to 0.20%, and the total amount of Sn and Bi is in the range of 0.5 to 1.5%, the balance being Al and inevitable It is characterized by comprising an impurity.
また請求項４の発明の快削アルミニウム合金押出材は、Ｓｉ０．４〜０．８％、Ｃｕ０．１〜０．４％、Ｍｇ０．８〜１．２％、Ｓｎ０．１〜０．５％、Ｂｉ０．３〜１．０％、Ｆｅ０．７５〜０．９％、Ｔｉ０．０１〜０．２０％を含有し、かつＳｎとＢｉの合計量が０．５〜１．５％の範囲内にあり、残部がＡｌおよび不可避的不純物よりなることを特徴とするものである。 Further, the free-cutting aluminum alloy extruded material of the invention of claim 4 is Si 0.4 to 0.8%, Cu 0.1 to 0.4%, Mg 0.8 to 1.2%, Sn 0.1 to 0.5%. , Bi 0.3 to 1.0%, Fe 0.75 to 0.9%, Ti 0.01 to 0.20%, and the total amount of Sn and Bi is in the range of 0.5 to 1.5% And the balance is made of Al and inevitable impurities.
この発明の快削アルミニウム合金押出材は、Ａｌ−Ｍｇ−Ｓｉ系合金押出材として、Ｐｂを添加することなく、従来の快削合金、例えばＪＩＳ６２６２合金などと同等の良好な切削性を得ることができると同時に、耐アルコール腐食性に優れたものであり、そのため１２０℃程度以上の高温でＯＨ基を含有するアルコール液と接する環境下で使用される切削加工部品として、そのような環境下で腐食もしくは溶解することが有効に抑制され、したがってブレーキ部品等として安全に使用することができる。 The free-cutting aluminum alloy extruded material of the present invention can obtain a good machinability equivalent to that of a conventional free-cutting alloy such as JIS6262 without adding Pb as an Al-Mg-Si alloy extruded material. At the same time, it has excellent resistance to alcohol corrosion. Therefore, it is corroded in such an environment as a machined part used in an environment where it comes into contact with an alcohol solution containing an OH group at a high temperature of about 120 ° C. or higher. Alternatively, dissolution is effectively suppressed, so that it can be safely used as a brake part or the like.
以下に、この発明の実施形態について説明する。 Embodiments of the present invention will be described below.
先ずこの発明の快削アルミニウム合金押出材における各合金元素の限定理由について説明する。 First, the reasons for limitation of each alloy element in the free-cutting aluminum alloy extruded material of the present invention will be described.
Ｓｉ、Ｍｇ：
ＳｉとＭｇは、Ｍｇ2Ｓｉを析出して強度向上に寄与する。Ｓｉ量が０．４％未満またはＭｇ量が０．８％未満では、強度向上の効果が小さく、一方、Ｓｉ量が０．８％を越えるかまたはＭｇ量が１．２％を越えれば、押出性等の加工性が低下する。したがってＳｉ量は０．４〜０．８％の範囲内、Ｍｇ量は０．８〜１．２％の範囲内とした。
Si, Mg:
Si and Mg precipitate Mg 2 Si and contribute to strength improvement. If the Si amount is less than 0.4% or the Mg amount is less than 0.8%, the effect of improving the strength is small. On the other hand, if the Si amount exceeds 0.8% or the Mg amount exceeds 1.2%, Processability such as extrudability is reduced. Therefore, the Si amount is in the range of 0.4 to 0.8%, and the Mg amount is in the range of 0.8 to 1.2%.
Ｓｎ、Ｂｉ：
Ｓｎ、Ｂｉの添加は切削性、特に切粉分断性の向上に寄与する。すなわちＳｎ、Ｂｉは、アルミニウムにはほとんど固溶せずにＳｎ−Ｂｉ系化合物として存在し、かつその融点は低く、そのため切削加工時には加工熱により化合物が溶融して、切粉にノッチが入って切粉分断性が向上すると考えられる。ここで、Ｓｎの融点は２３２℃、Ｂｉの融点は２７１℃と、ともに低融点ではあるが、Ｓｎ−Ｂｉ化合物では融点が１３９℃と、より一層低融点となるため、切粉分断性向上の効果が大きい。そのため切粉分断性を充分に向上させるために、Ｓｎ、Ｂｉを同時に添加することとした。切粉分断性は、Ｓｎ、Ｂｉの添加量が多いほど向上し、Ｓｎ、Ｂｉ同時添加の効果を発揮させるためには、Ｂｉを０．３％以上とする必要があり、またＳｎは０．１％以上とすることが必要である。またＳｎ、Ｂｉの合計添加量が０．５％未満では充分な切粉分断性が得られず、一方合計添加量が１．５％を越えれば耐食性が低下する。一方、Ｓｎを多量に添加すれば、ＯＨ基を含む高温のアルコール液と接した場合に溶解反応を引起こしてしまうおそれがあり、特にＳｎ添加量が０．５％を越えればその傾向が著しくなる。そしてＳｎ量を０．５％以下に制限すれば、ＯＨ基との反応が顕著に軽減されて、１２０℃の高温アルコール液に１２０時間接したときの腐食もしくは溶解による重量減少率が０．５％以下となる。一方、Ｂｉが１．０％を越えれば、耐食性が劣化するので好ましくない。したがってこれらの理由から、Ｓｎは０．１〜０．５％の範囲内、Ｂｉは０．３〜１．０％の範囲内、さらにＳｎとＢｉの合計添加量を０．５〜１．５％の範囲内に規制することとした。
Sn, Bi:
Addition of Sn and Bi contributes to the improvement of the machinability, particularly the chip breaking property. In other words, Sn and Bi are hardly dissolved in aluminum and exist as Sn-Bi compounds, and their melting points are low. Therefore, the compound melts by machining heat during cutting, and notches are formed in the chips. It is considered that the chip breaking property is improved. Here, Sn has a melting point of 232 ° C. and Bi has a melting point of 271 ° C., both of which are low melting points, but the Sn—Bi compound has a melting point of 139 ° C., which is a much lower melting point. Great effect. For this reason, Sn and Bi are added simultaneously in order to sufficiently improve the chip breaking property. The chip breaking property is improved as the addition amount of Sn and Bi is increased. In order to exhibit the effect of simultaneous addition of Sn and Bi, Bi needs to be 0.3% or more. It is necessary to set it to 1% or more. Further, if the total addition amount of Sn and Bi is less than 0.5%, sufficient chip breaking property cannot be obtained, while if the total addition amount exceeds 1.5%, the corrosion resistance decreases. On the other hand, if a large amount of Sn is added, there is a risk of causing a dissolution reaction when it comes into contact with a high-temperature alcohol solution containing OH groups. In particular, if the Sn addition amount exceeds 0.5%, the tendency is remarkable. Become. And if the amount of Sn is limited to 0.5% or less, the reaction with OH groups is remarkably reduced, and the weight reduction rate due to corrosion or dissolution when exposed to a 120 ° C. high temperature alcohol solution for 120 hours is 0.5 % Or less. On the other hand, if Bi exceeds 1.0%, corrosion resistance deteriorates, which is not preferable. Therefore, for these reasons, Sn is in the range of 0.1 to 0.5%, Bi is in the range of 0.3 to 1.0%, and the total addition amount of Sn and Bi is 0.5 to 1.5%. It was decided to regulate within the range of%.
Ｃｕ：
Ｃｕは、マトリックス中に固溶することにより強度向上に寄与する元素であるが、本発明者等は、Ｃｕの添加は強度向上のみならず、ＯＨ基を含むアルコール液への溶解を抑制する効果を奏することを新規に見出し、この発明ではＣｕを積極添加することとした。ここで、Ｃｕ量が０．１％未満ではその効果が充分に得られず、一方Ｃｕ添加量が０．４％を越えれば、一般的な耐食性が低下してしまう。そこでＣｕの添加量は０．１〜０．４％の範囲内とした。
Cu:
Cu is an element that contributes to strength improvement by solid solution in the matrix. However, the present inventors have the effect that addition of Cu not only improves strength but also suppresses dissolution in an alcohol solution containing an OH group. In the present invention, Cu was positively added. Here, if the amount of Cu is less than 0.1%, the effect cannot be sufficiently obtained. On the other hand, if the amount of Cu added exceeds 0.4%, general corrosion resistance is lowered. Therefore, the amount of Cu added is in the range of 0.1 to 0.4%.
Ｆｅ：
Ｆｅは、Ａｌ−Ｆｅ系あるいはＡｌ−Ｆｅ−Ｓｉ系などの化合物を形成して、切粉分断性の向上に寄与する元素であり、そこで請求項２、請求項４の発明の合金においてＦｅを積極添加することとした。ここで、Ｆｅを０．７５％以上添加することにより切粉分断性を向上させることができるが、Ｆｅ量が０．９％を越えれば押出成形性を低下させてしまうから、Ｆｅを積極添加する場合のＦｅ量は０．７５〜０．９％の範囲内とした。なお通常のアルミニウム合金においてもＦｅは不可避的不純物として含有される元素であり、したがって請求項１、請求項３の発明の合金の場合も、０．７５％未満のＦｅが不可避的不純物として含有されることは許容される。
Fe:
Fe is an element that forms a compound such as an Al-Fe system or an Al-Fe-Si system and contributes to the improvement of chip breaking property. Therefore, in the alloys of the inventions of claims 2 and 4, Fe is added. The active addition was decided. Here, adding 0.75% or more of Fe can improve the chip breaking property, but if Fe content exceeds 0.9%, the extrudability will be reduced, so Fe is actively added. In this case, the amount of Fe was set in the range of 0.75 to 0.9%. Even in ordinary aluminum alloys, Fe is an element contained as an inevitable impurity. Therefore, even in the case of the alloys according to claims 1 and 3, less than 0.75% of Fe is contained as an inevitable impurity. It is permissible.
Ｔｉ：
Ｔｉは、通常のアルミニウム合金において鋳塊結晶粒微細化材として添加することが多い元素であり、この発明の場合も、Ｔｉ添加による結晶粒微細化を通じて、強度向上および切粉分断性向上の効果を得ることができ、そこで請求項３、請求項４の発明の合金においてＴｉを添加することとした。但しＴｉ添加量が０．０１％未満では前述の効果が充分に得られず、一方Ｔｉ添加量が０．２０％を越えてもそれ以上効果は向上しないから、Ｔｉを添加する場合のＴｉ添加量は０．０１〜０．２０％の範囲内とした。なお請求項１、請求項２の発明の合金でも、不可避的不純物として０．０１％未満のＴｉが含有されることは許容される。
Ti:
Ti is an element often added as an ingot crystal grain refining material in a normal aluminum alloy. In the case of this invention as well, the effect of improving strength and improving chip breaking through crystal grain refining by addition of Ti. Therefore, Ti was added to the alloys of the inventions of claims 3 and 4. However, if the Ti addition amount is less than 0.01%, the above effect cannot be obtained sufficiently. On the other hand, if the Ti addition amount exceeds 0.20%, the effect is not further improved. The amount was in the range of 0.01 to 0.20%. Note that the alloys of the inventions of claims 1 and 2 are allowed to contain Ti of less than 0.01% as an inevitable impurity.
以上の各合金元素のほかは、基本的にはＡｌおよび不可避的不純物とすればよい。 In addition to the above alloy elements, Al and inevitable impurities may be basically used.
上述のように、Ａｌ−Ｍｇ−Ｓｉ系合金に対して、適切な量だけＳｎ、Ｂｉを添加し、かつＣｕを少量だけ添加したこの発明のアルミニウム合金押出材は、Ｐｂの添加なしで良好な切削性を得ると同時に、良好な耐アルコール腐食性を得て、ＯＨ基を含むアルコール液に高温で接した場合でも、溶解もしくは腐食することを有効に抑制することができる。ここで、耐アルコール腐食性の指標としては、ＯＨ基を１つ以上含むアルコール液に１２０℃で１２０時間接した場合の腐食減量が０．５重量％以下であれば、耐アルコール腐食性が良好と認めることができる。そして前述のようなこの発明で規定する成分組成範囲内の合金であれば、上記の指標を充分に満たすことができる。 As described above, the aluminum alloy extruded material of the present invention in which Sn and Bi are added in appropriate amounts and only a small amount of Cu is added to the Al—Mg—Si based alloy is good without adding Pb. At the same time as obtaining machinability, good alcohol corrosion resistance can be obtained, and dissolution or corrosion can be effectively suppressed even when contacted with an alcohol solution containing an OH group at a high temperature. Here, as an index of the alcohol corrosion resistance, if the corrosion weight loss when contacting with an alcohol liquid containing one or more OH groups at 120 ° C. for 120 hours is 0.5% by weight or less, the alcohol corrosion resistance is good. Can be recognized. And if it is an alloy within the component composition range prescribed | regulated by this invention as mentioned above, said parameter | index can fully be satisfy | filled.
なおＯＨ基を含むアルコールの例としては、トリエチレングリコールモノメチルエーテル（Ｃ７Ｈ１５Ｏ３−ＯＨ）などが挙げられるが、これに限定されるものではない。 Examples of alcohols containing OH groups include, but are not limited to, triethylene glycol monomethyl ether (C7H15O3-OH).
なおまた、この発明の快削アルミニウム合金押出材を製造する方法は特に限定されるものではなく、常法に従って製造すれば良い。例えば通常の方法により溶解・鋳造し、必要に応じて均質化処理を行なってから押出加工（通常は熱間押出）を行なえば良い。さらに押出加工後の処理・調質についても特に限定されるものではなく、通常の製造条件により、用途に応じて調質を選択すれば良い。例えば、熱間押出上がりままのＴ１でも良いし、溶体化・人工時効を施したＴ６でも良く、さらには溶体化・冷間加工・人工時効を施したＴ８、Ｔ９でも良い。なお切粉分断性は、一般に硬度が高い方が良好であることから、溶体化後に冷間加工や人工時効を施すＴ３、Ｔ８、Ｔ９等の調質が特に好ましい。 In addition, the method for producing the free-cutting aluminum alloy extruded material of the present invention is not particularly limited, and may be produced according to a conventional method. For example, melting and casting may be performed by a normal method, and homogenization may be performed as necessary, followed by extrusion (usually hot extrusion). Further, the processing and tempering after the extrusion are not particularly limited, and the tempering may be selected according to the application under normal production conditions. For example, T1 as it is after hot extrusion may be used, T6 may be subjected to solution / artificial aging, and T8 and T9 may be subjected to solution / cold working / artificial aging. In addition, since the chip parting property is generally better when the hardness is higher, tempering such as T3, T8, and T9, which is subjected to cold working or artificial aging after solution forming, is particularly preferable.
以下にこの発明の実施例を、比較例とともに示す。なお以下の各実施例は、飽くまで説明のためのものであり、この発明の技術的範囲を制限するものでないことはもちろんである。 Examples of the present invention are shown below together with comparative examples. The following examples are for illustrative purposes only, and are not intended to limit the technical scope of the present invention.
表１の合金Ｎｏ．１〜Ｎｏ．２８に示す組成の各合金を溶解し、常法に従ってＤＣ鋳造を行なって直径２２０ｍｍの鋳塊（ビレット）を得た。この鋳塊に５５０℃×６時間の均質化処理を施した後、４００℃で熱間押出を行なって直径３５ｍｍの丸棒材とした。これに５２０℃×２時間の溶体化処理を施した後、直ちに水冷することにより焼入れし、さらに１８０℃×８時間の人工時効処理を行った。 Alloy No. 1 in Table 1 1-No. Each alloy having the composition shown in 28 was melted, and DC casting was performed according to a conventional method to obtain an ingot (billette) having a diameter of 220 mm. The ingot was homogenized at 550 ° C. for 6 hours and then hot extruded at 400 ° C. to obtain a round bar having a diameter of 35 mm. This was subjected to a solution treatment at 520 ° C. for 2 hours, and then immediately quenched with water, followed by an artificial aging treatment at 180 ° C. for 8 hours.
以上のようにして得られた各押出材について、次のように切削試験およびアルコールへの浸漬試験を行なった。
（１）切削試験
上記の押出材を用いて、外削による切削試験を行なって、切粉分断性を評価した。切削条件は、回転数２０００ｒｐｍ、切り込み量１ｍｍ、送り量０．０４ｍｍ／ｒｅｖ、とした。
（２）アルコールへの浸漬試験
ＯＨ基を含むアルコール液に対する浸漬試験を行なって、耐アルコール腐食性を評価した。具体的には、前述のようにして得られた直径３５ｍｍの棒状押出材を切削加工して、直径３０ｍｍ、厚さ５ｍｍの円盤状試験片とし、その試験片を、ＯＨ基を有するアルコール類であるトリエチレングリコールモノメチルエーテル（Ｃ７Ｈ１５Ｏ３−ＯＨ）を主成分として含有する市販の自動車用ブレーキ液（米国連邦安全基準：Ｆｅｄｅｒａｌ Ｍｏｔｏｒ Ｖｅｈｉｃｌｅ Ｓａｆｅｔｙ ＳｔａｎｄａｒｄのＤＯＴ３規格品）に浸漬し、１２０℃×１２０時間の浸漬保持を行なった。
Each extruded material obtained as described above was subjected to a cutting test and an immersion test in alcohol as follows.
(1) Cutting test Using the above-mentioned extruded material, a cutting test by external cutting was performed to evaluate the chip breaking property. The cutting conditions were a rotation speed of 2000 rpm, a cut amount of 1 mm, and a feed amount of 0.04 mm / rev.
(2) Immersion test in alcohol An immersion test in an alcohol solution containing an OH group was conducted to evaluate alcohol corrosion resistance. Specifically, the rod-shaped extruded material having a diameter of 35 mm obtained as described above is cut into a disk-shaped test piece having a diameter of 30 mm and a thickness of 5 mm, and the test piece is made of an alcohol having an OH group. Immersion in a commercially available automotive brake fluid (US Federal Safety Standard: Federal Motor Safety Standard DOT3 standard product) containing triethylene glycol monomethyl ether (C7H15O3-OH) as the main component and 120 ° C x 120 hours immersion Holding was performed.
これらの切削試験による切粉分断性評価結果、およびアルコール液への浸漬試験による耐アルコール腐食性評価（−ＯＨ溶液溶解性評価）結果を表２に示す。なおこれらの試験、評価のほか、一般的な耐食性評価として、常法に従って塩水噴霧試験を行ない、また強度評価として、常法に従って、引張強さ、耐力、伸びおよび硬さを調べた。 Table 2 shows the results of evaluation of chip breaking by these cutting tests, and evaluation of alcohol corrosion resistance (-OH solution solubility evaluation) by immersion test in an alcohol solution. In addition to these tests and evaluations, as a general corrosion resistance evaluation, a salt spray test was conducted according to a conventional method, and as a strength evaluation, tensile strength, proof stress, elongation and hardness were examined according to a conventional method.
ここで、切粉分断性の評価にあたっては、切粉１００個当りの質量で４段階評価した。評価基準は、Ａ：４ｇ以下、Ｂ：４ｇを越え８ｇ以下、Ｃ：８ｇを越え３０ｇ以下、Ｄ：３０ｇより大、とした。 Here, in the evaluation of the chip breaking property, the mass per 100 chips was evaluated in four stages. The evaluation criteria were A: 4 g or less, B: more than 4 g and 8 g or less, C: more than 8 g and 30 g or less, and D: greater than 30 g.
また耐アルコール腐食性評価については、前述のように１２０℃×１２０時間の浸漬保持による重量減少率を調べ、重量減少量が０％のものをａ、０．５％以下（０％を含まず）のものをｂ、０．５％を越えたものをｃとして３段階評価を行なった。 As for the alcohol corrosion resistance evaluation, as described above, the weight reduction rate by dipping and holding at 120 ° C. for 120 hours was examined. ) Was evaluated on a three-stage scale, with b being more than 0.5% and c being more than 0.5%.
合金Ｎｏ．１〜Ｎｏ．１２は、いずれもＳｎ、Ｂｉ、Ｃｕをこの発明で規定する範囲内で添加し、さらにＳｉ、Ｍｇ、Ｆｅ、Ｔｉの各元素の量もこの発明で規定する範囲内とした発明合金であり、これらの発明合金は、いずれも良好な切粉分断性を示すとともに、良好な耐アルコール腐食性を示すことが判明し、またそのほか一般的な耐食性や、強度、押出性等の点でも特に問題がないことが確認された。なおこれらの発明合金Ｎｏ．１〜Ｎｏ．１２のうち、Ｆｅを０．７５%以上０．９%以下添加した発明合金Ｎｏ．１１、Ｎｏ．１２は、前記の切粉分断性の評価指標では他の発明合金と変わらなかったが、目視による切粉形状の評価において、他の発明合金よりも切粉が分断され易く良好であることが確認された。 Alloy No. 1-No. No. 12 is an invention alloy in which Sn, Bi, Cu is added within the range specified in the present invention, and the amounts of each element of Si, Mg, Fe, Ti are also within the range specified in the present invention, These invention alloys were all found to exhibit good chip breaking properties and good alcohol corrosion resistance, and in addition, there were other problems with general corrosion resistance, strength, extrudability, etc. Not confirmed. These invention alloys No. 1-No. 12 of the invention alloy No. 12 with Fe added at 0.75% or more and 0.9% or less. 11, no. No. 12 was the same as the other invention alloys in the above-mentioned evaluation index of chip breaking property, but in the evaluation of the chip shape by visual observation, it was confirmed that the chips were more easily cut off than the other invention alloys. It was done.
一方、合金Ｎｏ．１３〜Ｎｏ．２８は、成分元素のうちのいずれか一つ以上がこの発明で規定する範囲を外れた比較合金であり、これらの比較合金では、切粉分断性（切削性）、耐アルコール腐食性、あるいは塩水噴霧試験耐性などの一般的な耐食性、強度、押出性のいずれかの特性が劣っていることが判明した。 On the other hand, Alloy No. 13-No. 28 is a comparative alloy in which any one or more of the constituent elements are out of the range specified in the present invention. In these comparative alloys, the chip breaking property (cutting property), the alcohol corrosion resistance, or the salt water It was found that any one of general corrosion resistance such as spray test resistance, strength, and extrudability was inferior.
すなわち、先ず比較合金Ｎｏ．１６、Ｎｏ．２１、Ｎｏ．２２の場合は、ＳｎあるいはＢｉの添加量がこの発明で規定する量より少ないため、アルコール液による腐食はほとんどないものの、切粉分断性に劣っていた。このうち、比較合金Ｎｏ．１６、Ｎｏ．２２は、Ｓｎ添加量およびＳｎ＋Ｂｉ添加量がともにこの発明で規定する下限量に満たないため、切粉分断性評価がＣと悪かったが、比較合金Ｎｏ．２１は、Ｂｉ添加量は本発明で規定する下限量に若干満たないものの、Ｓｎ添加量およびＳｎ＋Ｂｉ添加量がこの発明で規定する範囲を満たしていることから、切粉分断性評価はＢとなった。一方、Ｓｎ添加量がこの発明で規定する上限（０．５％）より多い比較合金Ｎｏ．１７、Ｎｏ．１８、あるいはＳｎ＋Ｂｉ添加量がこの発明で規定する上限量（１．５％）より多い比較合金Ｎｏ．１３、Ｎｏ．１４、Ｎｏ．１７では、切粉分断性は優れるものの、アルコール液への溶解が激しくなってしまった。 That is, first, comparative alloy No. 16, no. 21, no. In the case of No. 22, since the addition amount of Sn or Bi was less than the amount specified in the present invention, although there was almost no corrosion by the alcohol liquid, the chip breaking property was inferior. Among these, comparative alloy No. 16, no. In No. 22, the amount of Sn added and the amount of Sn + Bi added were both less than the lower limit specified in the present invention, so that the chip breaking evaluation was bad as C. In No. 21, although the Bi addition amount is slightly less than the lower limit amount specified in the present invention, the amount of Sn addition and the Sn + Bi addition amount satisfy the range specified in the present invention. It was. On the other hand, comparative alloy No. with a Sn addition amount larger than the upper limit (0.5%) specified in the present invention. 17, no. 18, or comparative alloy No. in which Sn + Bi addition amount is larger than the upper limit amount (1.5%) specified in the present invention. 13, no. 14, no. In No. 17, although the chip breaking property was excellent, dissolution in the alcohol liquid became intense.
また比較合金Ｎｏ．２０の場合、切粉分断性およびアルコール液への溶解性は、ともに問題がなかったが、Ｂｉが１．０％を越えているため、塩水噴霧試験耐性などの一般的な耐食性で若干劣っていることが確認された。 Comparative alloy No. In the case of 20, there was no problem in both the chip breaking property and the solubility in the alcohol solution, but since Bi exceeded 1.0%, the general corrosion resistance such as salt spray test resistance was slightly inferior. It was confirmed that
さらに、比較合金Ｎｏ．２３の場合は、切粉分断性およびアルコール液への溶解性は、ともに問題がなかったが、Ｆｅ量が０．９％を越えているため、押出性が低下した。 Further, comparative alloy No. In the case of No. 23, there was no problem in both the chip breaking property and the solubility in the alcohol solution, but since the amount of Fe exceeded 0.9%, the extrudability was lowered.
一方、比較合金Ｎｏ．１５、Ｎｏ．１９、Ｎｏ．２４〜Ｎｏ．２８は、主に強度に影響するＳｉ、Ｃｕ、Ｍｇ量がこの発明で規定する範囲から外れているものであり、これらの合金元素の添加量の多少は、切粉分断性には大きな影響を与えないが、添加量の少ないものは強度低下、また添加量の多いものは押出性の低下が見られた。 On the other hand, Comparative Alloy No. 15, no. 19, no. 24-No. In No. 28, the amounts of Si, Cu, and Mg that mainly affect the strength are out of the range defined in the present invention, and the amount of these alloy elements added has a great influence on the chip breaking property. Although not given, when the amount added was small, the strength decreased, and when the amount added was large, the extrudability decreased.
具体的には、比較合金Ｎｏ．１５は、Ｍｇ添加量が不足しているため、充分な強度が得られなかった。また比較合金Ｎｏ．１９は、Ｃｕが添加されていないため、充分な強度が得られず、同時にＯＨ基を含むアルコール液への溶解が生じた。ここで、比較合金Ｎｏ．１９のアルコール液への溶解量は、表２に示すように評価としてはｂに相当したが、重量減少率は０．５％に近くてｃ評価に近く、このことは、Ｃｕがこの発明の規定量に不足していればＯＨ基を含むアルコール液に対する耐食性が充分には得られなくなることを示している。さらに比較合金Ｎｏ．２４は、Ｓｉ添加量が不足しているため、充分な強度が得られなかった。一方比較合金Ｎｏ．２５、Ｎｏ．２６、Ｎｏ．２８は、Ｓｉ量またはＭｇ量が多過ぎたため、押出性等の加工性に劣り、試験合金を作製できなかった。そしてまた比較合金Ｎｏ．２７は、Ｃｕ量が多過ぎたため、塩水噴霧試験耐性などの一般的な耐食性が劣ることが確認された。 Specifically, Comparative Alloy No. No. 15 was insufficient in Mg addition amount, so sufficient strength could not be obtained. Comparative alloy No. In No. 19, since Cu was not added, sufficient strength was not obtained, and at the same time, dissolution in an alcohol solution containing OH groups occurred. Here, comparative alloy No. As shown in Table 2, the amount of 19 dissolved in the alcohol solution corresponded to b as an evaluation, but the weight loss rate was close to 0.5% and was close to c evaluation. If the specified amount is insufficient, the corrosion resistance to the alcohol liquid containing OH groups cannot be obtained sufficiently. Furthermore, comparative alloy No. In No. 24, since the amount of Si added was insufficient, sufficient strength could not be obtained. On the other hand, comparative alloy No. 25, no. 26, no. No. 28 was inferior in workability such as extrudability because the amount of Si or Mg was too large, and a test alloy could not be produced. And again, comparative alloy No. It was confirmed that No. 27 was inferior in general corrosion resistance such as salt spray test resistance because the amount of Cu was too much.
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