JP2012524837A5 - - Google Patents
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- JP2012524837A5 JP2012524837A5 JP2012506317A JP2012506317A JP2012524837A5 JP 2012524837 A5 JP2012524837 A5 JP 2012524837A5 JP 2012506317 A JP2012506317 A JP 2012506317A JP 2012506317 A JP2012506317 A JP 2012506317A JP 2012524837 A5 JP2012524837 A5 JP 2012524837A5
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- 229910000838 Al alloy Inorganic materials 0.000 claims description 141
- 239000007788 liquid Substances 0.000 claims description 50
- 239000000956 alloy Substances 0.000 claims description 43
- 238000002791 soaking Methods 0.000 claims description 39
- 238000005266 casting Methods 0.000 claims description 26
- 229910052761 rare earth metal Inorganic materials 0.000 claims description 26
- 229910045601 alloy Inorganic materials 0.000 claims description 23
- REDXJYDRNCIFBQ-UHFFFAOYSA-N aluminium(3+) Chemical class [Al+3] REDXJYDRNCIFBQ-UHFFFAOYSA-N 0.000 claims description 23
- 238000005096 rolling process Methods 0.000 claims description 22
- WCUXLLCKKVVCTQ-UHFFFAOYSA-M potassium chloride Chemical compound [Cl-].[K+] WCUXLLCKKVVCTQ-UHFFFAOYSA-M 0.000 claims description 18
- FAPWRFPIFSIZLT-UHFFFAOYSA-M sodium chloride Chemical compound [Na+].[Cl-] FAPWRFPIFSIZLT-UHFFFAOYSA-M 0.000 claims description 18
- 239000003795 chemical substances by application Substances 0.000 claims description 14
- 229910018084 Al-Fe Inorganic materials 0.000 claims description 12
- 229910018192 Al—Fe Inorganic materials 0.000 claims description 12
- 239000012535 impurity Substances 0.000 claims description 11
- 229910052782 aluminium Inorganic materials 0.000 claims description 10
- 229910052742 iron Inorganic materials 0.000 claims description 9
- 150000002910 rare earth metals Chemical class 0.000 claims description 9
- 239000011780 sodium chloride Substances 0.000 claims description 9
- 238000004519 manufacturing process Methods 0.000 claims description 7
- 229910052684 Cerium Inorganic materials 0.000 claims description 6
- 229910052746 lanthanum Inorganic materials 0.000 claims description 6
- 229910008288 Si—Fe—Al Inorganic materials 0.000 claims description 5
- 239000000203 mixture Substances 0.000 claims description 5
- 239000000843 powder Substances 0.000 claims description 5
- 238000000137 annealing Methods 0.000 claims description 3
- 238000009472 formulation Methods 0.000 claims description 3
- 229910018085 Al-F Inorganic materials 0.000 claims 1
- 229910018179 Al—F Inorganic materials 0.000 claims 1
- 239000004615 ingredient Substances 0.000 claims 1
- 239000002893 slag Substances 0.000 description 16
- 238000007670 refining Methods 0.000 description 13
- 239000000463 material Substances 0.000 description 11
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminum Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 8
- 238000009749 continuous casting Methods 0.000 description 8
- 239000000498 cooling water Substances 0.000 description 8
- 230000000694 effects Effects 0.000 description 8
- 239000007789 gas Substances 0.000 description 8
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 8
- PNEYBMLMFCGWSK-UHFFFAOYSA-N al2o3 Chemical compound [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 description 4
- 238000007664 blowing Methods 0.000 description 4
- QXUAMGWCVYZOLV-UHFFFAOYSA-N boride(3-) Chemical compound [B-3] QXUAMGWCVYZOLV-UHFFFAOYSA-N 0.000 description 4
- 239000004020 conductor Substances 0.000 description 4
- 229910001873 dinitrogen Inorganic materials 0.000 description 4
- 238000002844 melting Methods 0.000 description 4
- 229910052751 metal Inorganic materials 0.000 description 4
- 239000002184 metal Substances 0.000 description 4
- IJGRMHOSHXDMSA-UHFFFAOYSA-N nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 4
- 238000003756 stirring Methods 0.000 description 4
- 238000004321 preservation Methods 0.000 description 3
- 101700034707 IACS Proteins 0.000 description 2
- 238000005452 bending Methods 0.000 description 2
- 229910052804 chromium Inorganic materials 0.000 description 2
- 238000007906 compression Methods 0.000 description 2
- RYGMFSIKBFXOCR-UHFFFAOYSA-N copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 2
- 229910052802 copper Inorganic materials 0.000 description 2
- 239000010949 copper Substances 0.000 description 2
- 229910052748 manganese Inorganic materials 0.000 description 2
- 238000000034 method Methods 0.000 description 2
- 229910052719 titanium Inorganic materials 0.000 description 2
- 229910052720 vanadium Inorganic materials 0.000 description 2
- 238000004458 analytical method Methods 0.000 description 1
- 150000001875 compounds Chemical class 0.000 description 1
- 238000010438 heat treatment Methods 0.000 description 1
- 230000014759 maintenance of location Effects 0.000 description 1
- 238000003860 storage Methods 0.000 description 1
Description
上記目的を達成するために，本発明は以下の技術的解決手段を採用する。すなわち，ケーブル用の高い延伸性を有するアルミニウム合金材料は以下の成分により構成される：
Ｆｅ：０．３０〜０．８０ｗｔ％，Ｓｉ：０．０３〜０．１０ｗｔ％，希土類元素（すなわちＣｅ及びＬａ）：０．０１〜０．３０ｗｔ％，及びその他Ａｌ及び不可避的不純物。
In order to achieve the above object, the present invention employs the following technical solutions. That is, a highly extensible aluminum alloy material for cables is composed of the following components:
Fe: 0.30 to 0.80 wt%, Si: 0.03 to 0.10 wt%, rare earth elements (ie Ce and La): 0.01 to 0.30 wt%, and other Al and inevitable impurities.
本発明の別の目的は，以下の工程を含む，高い延伸性を有するアルミニウム合金材料の製造方法を提供することである。
１）溶融鋳造
最初に９２〜９８重量部（ｐｂｗ）のＳｉ−Ｆｅ−Ａｌ合金と０．７３〜５．２６ｐｂｗのＡｌ―Ｆｅ合金を添加し，７１０〜７５０℃に加熱して融解する；次に７２０〜７６０℃に加熱し，１〜３ｐｂｗの希土類―Ａｌ合金及び０．１７〜０．６７ｐｂｗのＢ−Ａｌ合金を添加し，前記希土類―Ａｌ合金は，ＡｌとＣｅ及びＬａから成る希土類元素との合金であり；次に，０．０４〜０．０６ｐｂｗの精製剤を添加して８〜２０分間精製し；次に，前記温度で２０〜４０分間保持し，その後，鋳造する。
２）半焼鈍(semi-annealing)処理
鋳造によって得たアルミニウム合金を２８０〜３８０℃で４〜１０時間保持し，その後，取り出して周囲温度まで自然に冷却する。
Another object of the present invention is to provide a method for producing an aluminum alloy material having high extensibility, including the following steps.
1) Melt casting First, 92-98 parts by weight (pbw) of Si-Fe-Al alloy and 0 . It was added Al-Fe alloy of 73 to 5.26 pbw, melted by heating to seven hundred ten to seven hundred and fifty ° C.; then heated to 720-760 ° C., rare earth 1～3Pbw -Al alloy and 0.17 was added 0.67pbw of B-Al alloy, the rare earth -Al alloy is an alloy of rare-earth element consisting of Al and Ce and La; then added refining agent for 0.04~0.06pbw And then purified for 8-20 minutes; then held at said temperature for 20-40 minutes, then cast.
2) Semi-annealing treatment The aluminum alloy obtained by casting is kept at 280-380 ° C. for 4-10 hours, then taken out and naturally cooled to ambient temperature.
本発明で提供されるケーブル用の高い延伸性を有するアルミニウム合金材料は，以下の利点を有する新型のＡｌ−Ｆｅ合金材料である。
１）本発明において，Ｆｅの含有量は０．３０〜０．８０％の範囲に制御され，そのため，アルミニウム合金の強度を増加させることが可能となり，アルミニウム合金の耐クリープ性及び熱安定性も向上させることが可能である。従来のＥＣアルミニウム材料と比較した場合，耐クリープ性は３００％向上する。また，Ｆｅはアルミニウム合金の靱性を向上させることができ，圧縮ねじり加工（compression and twisting process）におけるアルミニウム合金材料の圧縮係数は０．９３以上と高くなり得て，これは従来のＥＣアルミニウム材料では達成できない。ＥＣアルミニウム材料で製造された導体と比較して，同じ外径のアルミニウム合金で製造された圧縮導体は，断面積が大きく，導電性及び安定性が高く，生産コストが低い。
２）本発明において，Ｓｉの含有量は０．０３〜０．１０％の範囲に制御され，そのため，アルミニウム合金の強度に対するＳｉの増強効果が確保される。
３）本発明において，希土類元素は，Ｓｉの含有量を減少させることが可能であり，そのため，アルミニウム合金の導電性へのＦｅ及び，特にＳｉの影響を非常に低レベルまで低下させる；更に，希土類元素の添加により，アルミニウム合金材料の結晶構造を向上させ，それにより，アルミニウム合金材料の処理特性が向上し，アルミニウム合金材料の処理には好適となる。
４）本発明において，希土類元素は，主にＣｅ及びＬａであり，これらは３）に記載の性能を充分に獲得することができる。
５）本発明において，元素Ｂは，Ｔｉ，Ｖ，Ｍｎ，Ｃｒなどの不純物元素と反応して化合物を形成することができるが，これらは堆積し，その後，取り除くことができる。したがって，アルミニウム合金の導電性への不純物元素（例えば，Ｔｉ，Ｖ，Ｍｎ，Ｃｒなど）の影響も低下させることが可能となり，アルミニウム合金の導電性を向上させることができる。
６）本発明によるアルミニウム合金を製造する場合には，半焼鈍処理によって合金材料が導電化される。したがって，引張ねじり加工（drawing and twisting process）中の導体の構造に対する応力の悪影響を低下させることができる。そのため，導電性は６１％ＩＡＣＳ（従来のＥＣアルミニウムで製造された導体の導電性の基準は，６１％ＩＡＣＳである。）まで，或いはそれ以上になり得る；更に，焼鈍処理は，アルミニウム合金材料の延伸性及び可撓性を大いに向上させることができる。本発明で提供されるアルミニウム合金材料で製造されたケーブルは，銅ケーブルと比較して３０％高い延伸性と，２５％高い可撓性を有し，曲げ半径は外径の７倍と小さい。一方，銅ケーブルの曲げ半径は外径の１５倍である。
The aluminum alloy material having high extensibility for cables provided in the present invention is a new type Al—Fe alloy material having the following advantages.
1) In the present invention, the Fe content is controlled in the range of 0.30 to 0.80 %, so that the strength of the aluminum alloy can be increased, and the creep resistance and thermal stability of the aluminum alloy are also improved. It is possible to improve. When compared with conventional EC aluminum materials, the creep resistance is improved by 300%. In addition, Fe can improve the toughness of aluminum alloy, and the compression coefficient of aluminum alloy material in compression and twisting process can be as high as 0.93 or higher, which is not the case with conventional EC aluminum material. Cannot be achieved. Compared to conductors made of EC aluminum material, compressed conductors made of aluminum alloys of the same outer diameter have a large cross-sectional area, high conductivity and stability, and low production costs.
2) In the present invention, the Si content is controlled in the range of 0.03 to 0.10%, so that the Si enhancement effect on the strength of the aluminum alloy is ensured.
3) In the present invention, rare earth elements can reduce the Si content, thus reducing the influence of Fe and especially Si on the conductivity of aluminum alloys to a very low level; The addition of rare earth elements improves the crystal structure of the aluminum alloy material, thereby improving the processing characteristics of the aluminum alloy material and is suitable for the processing of the aluminum alloy material.
4) In the present invention, rare earth elements are mainly Ce and La, and these can sufficiently achieve the performance described in 3).
5) In the present invention, element B can react with impurity elements such as Ti, V, Mn, and Cr to form a compound, but these can be deposited and then removed. Therefore, the influence of impurity elements (for example, Ti, V, Mn, Cr, etc.) on the conductivity of the aluminum alloy can be reduced, and the conductivity of the aluminum alloy can be improved.
6) When producing an aluminum alloy according to the present invention, the alloy material is made conductive by semi-annealing. Thus, the negative effects of stress on the structure of the conductor during the drawing and twisting process can be reduced. Therefore, the conductivity can be up to 61% IACS (conductivity standard for conductors made of conventional EC aluminum is 61% IACS) or higher; The stretchability and flexibility can be greatly improved. The cable made of the aluminum alloy material provided by the present invention has 30% higher extensibility and 25% higher flexibility than the copper cable, and the bending radius is as small as 7 times the outer diameter. On the other hand, the bending radius of the copper cable is 15 times the outer diameter.
実施例１
Ｉ．溶融鋳造処理
１．材料の配合
５１００ｋｇのＳｉ−Ｆａ−Ａｌ合金のインゴット（０．０７％のＳｉ及び０．１３％のＦｅを含有），４０．４ｋｇのＡｌ−Ｆｅ合金（２２％のＦｅを含有），５．６ｋｇの希土類−Ａｌ合金（１０％希土類元素を含有），８．８ｋｇのＢ−Ａｌ合金（３．５％のＢを含有），及び２．３ｋｇの精製剤（２３％のＮａ3Ａｌ・Ｆ6＋４７％のＫＣｌ＋３０％のＮａＣｌ）
２．供給方法
材料の供給中に，成分をできる限り均等に分配するために，溶銑炉内に，Ｓｉ−Ｆａ−Ａｌ合金のインゴットと共に，Ａｌ−Ｆｅ合金をバッチごとに均等に供給する。
３．熱保存処理
液状アルミニウム合金を均熱炉に流し入れる場合，該均熱炉の温度は７１０〜７５０℃に制御する；希土類−Ａｌ合金及びＢ−Ａｌ合金を液状アルミニウム合金に添加する場合，均熱炉の温度を７２０〜７６０℃に上昇させるが，該温度は７６０℃を越えない。ここで，温度の上昇は希土類−Ａｌ合金及びＢ−Ａｌ合金の融解に好適であり，それにより，希土類元素及び元素Ｂの処理効果を向上させることが可能となる。
４．希土類処理及びホウ化処理
４．１．均熱炉に液状アルミニウム合金が充満する３０分前に，３分の１の希土類−Ａｌ合金を添加する。
４．２．均熱炉に液状アルミニウム合金が充満する５分前に，残りの３分の２の希土類−Ａｌ合金及びＢ−Ａ合金を添加する。
希土類−Ａｌ合金及びＢ−Ａｌ合金を異なる時間帯に添加することで，希土類元素及び元素Ｂが全面的に機能することが可能となり，効果を高めることができる。
４．３．希土類−Ａｌ合金及びＢ−Ａｌ合金の供給位置が，均熱炉内で均等に分布することが可能となる。
５．精製（スラグ除去，ガス除去，攪拌及び除滓）
５．１．均熱炉全体で液状アルミニウム合金の成分を均質にするために，該液状アルミニウム合金を，均熱炉の隅部の位置にあるものも含めて５分間攪拌する。
５．２．均熱炉に液状アルミニウム合金が充満した後，液状アルミニウム合金の底部内で吹込みノズルを動かしながら，２．３ｋｇの精製剤（２３％のＮａ３Ａｌ・Ｆ６＋４７％のＫＣｌ＋３０％のＮａＣｌ）の粉末を，高純度窒素ガスで液状アルミニウム合金の底部に３〜５分間吹き込み，ガスによって，含有スラグを該液状アルミニウム合金の表面に沿って均一に上昇させる。浮遊している酸化アルミニウムスラグを炉から完全に除去することで，精製剤がもたらした新たな不純物を，可能な限り減少させることができる。
６．現場で採取した試料の迅速な分析と保持及び熱保存
液状アルミニウム合金のＦｅの含有量がスラグの除去後の要件を満たす場合，液状アルミニウム合金を２０〜４０分間保持する。
７．連続鋳造及び圧延処理の制御
７．１．温度制御
７．１．１．鋳造用取鍋の温度：７２０〜７３０℃
７．１．２．圧延機へ供給される条片の温度：４５０〜４９０℃
７．１．３．アルミニウムロッドの最終圧延温度：約３００℃
７．２．連続鋳造機内の冷却水の制御
鋳造ホイールの外部の水量に対する鋳造ホイールの内部の水量：３：２；
２次冷却水の量は，鋳造された条片の温度にあわせて調節する。
７．３．鋳造機の電圧：６０〜９０Ｖ
７．４．圧延機を通過する電流：２００〜２８０Ａ；圧延機の速度：７．５〜８．５ｍ／分
Example 1
I. Melt casting process Material mix 5100 kg Si-Fa-Al alloy ingot (containing 0.07% Si and 0.13% Fe), 40.4 kg Al-Fe alloy (containing 22% Fe), 5. 6 kg rare earth- Al alloy (containing 10% rare earth element), 8.8 kg B-Al alloy (containing 3.5% B), and 2.3 kg refining agent (23% Na 3 Al.F) 6 + 47% KCl + 30% NaCl)
2. Supplying method In order to distribute the components as evenly as possible during the supply of the material, the Al—Fe alloy is supplied evenly in batches together with the Si—Fa—Al alloy ingot in the hot metal furnace.
3. Heat preservation treatment When a liquid aluminum alloy is poured into a soaking furnace, the temperature of the soaking furnace is controlled at 710 to 750 ° C; when a rare earth-Al alloy and a B-Al alloy are added to the liquid aluminum alloy, the soaking furnace Is raised to 720-760 ° C, but the temperature does not exceed 760 ° C. Here, the increase in temperature is suitable for melting of the rare earth-Al alloy and the B-Al alloy, so that the treatment effect of the rare earth element and the element B can be improved.
4). Rare earth treatment and boride treatment 4.1. One-third of the rare earth-Al alloy is added 30 minutes before the soaking furnace is filled with the liquid aluminum alloy.
4.2. 5 minutes before the soaking furnace is filled with the liquid aluminum alloy, the remaining two thirds of the rare earth-Al alloy and the B-A alloy are added.
By adding the rare earth-Al alloy and the B-Al alloy in different time zones, the rare earth element and the element B can function entirely, and the effect can be enhanced.
4.3. The supply positions of the rare earth-Al alloy and the B-Al alloy can be evenly distributed in the soaking furnace.
5. Refinement (slag removal, gas removal, stirring and removal)
5.1. In order to make the components of the liquid aluminum alloy homogeneous throughout the soaking furnace, the liquid aluminum alloy is stirred for 5 minutes, including those at the corners of the soaking furnace.
5.2. After the soaking furnace is filled with the liquid aluminum alloy, 2.3 kg of refining agent (23% Na 3 Al · F 6 + 47% KCl + 30% NaCl) while moving the blowing nozzle in the bottom of the liquid aluminum alloy The powder is blown into the bottom of the liquid aluminum alloy with high-purity nitrogen gas for 3 to 5 minutes, and the contained slag is uniformly raised along the surface of the liquid aluminum alloy by the gas. By completely removing the suspended aluminum oxide slag from the furnace, the new impurities introduced by the refining agent can be reduced as much as possible.
6). Rapid analysis and retention of samples collected on site and thermal storage If the Fe content of the liquid aluminum alloy meets the requirements after removal of the slag, hold the liquid aluminum alloy for 20-40 minutes.
7). Control of continuous casting and rolling process 7.1. Temperature control 7.1.1. Casting ladle temperature: 720-730 ° C
7.1.2. Temperature of strip supplied to rolling mill: 450-490 ° C
7.1.3. Final rolling temperature of aluminum rod: about 300 ° C
7.2. Control of cooling water in the continuous casting machine Water volume inside the casting wheel relative to the water volume outside the casting wheel: 3: 2;
The amount of secondary cooling water is adjusted according to the temperature of the cast strip.
7.3. Casting machine voltage: 60-90V
7.4. Current passing through the rolling mill: 200 to 280 A; Speed of the rolling mill: 7.5 to 8.5 m / min
参考例
Ｉ．溶融鋳造処理
１．材料の配合
５１１０ｋｇのＳｉ−Ｆａ−Ａｌ合金のインゴット（０．１０％のＳｉ及び０．１３％のＦｅを含有），２５８ｋｇのＡｌ−Ｆｅ合金（２３．２％のＦｅを含有），１６６．５ｋｇの希土類−Ａｌ合金（９．８％の希土類元素を含有），１０ｋｇのＢ−Ａｌ合金（３．３％のＢを含有），及び２．３ｋｇの精製剤（２３％のＮａ3Ａｌ・Ｆ6＋４７％のＫＣｌ＋３０％のＮａＣｌ）
２．供給方法
材料の供給中に，成分をできる限り均等に分配するために，溶銑炉内に，Ｓｉ−Ｆａ−Ａｌ合金のインゴットと共に，Ａｌ−Ｆｅ合金をバッチごとに均等に供給する。
３．熱保存処理
液状アルミニウム合金を均熱炉に流し入れる場合，該均熱炉の温度は７１０〜７５０℃に制御する；希土類−Ａｌ合金及びＢ−Ａｌ合金を液状アルミニウム合金に添加する場合，均熱炉の温度を７２０〜７６０℃に上昇させるが，該温度は７６０℃を越えない。ここで，温度の上昇は希土類−Ａｌ合金及びＢ−Ａｌ合金の融解に好適であり，それにより，希土類元素及び元素Ｂの処理効果を向上させることが可能となる。
４．希土類処理及びホウ化処理
４．１．均熱炉に液状アルミニウム合金が充満する３０分前に，３分の１の希土類−Ａｌ合金を添加する。
４．２．均熱炉に液状アルミニウム合金が充満する５分前に，残りの３分の２の希土類−Ａｌ合金及びＢ−Ａ合金を添加する。
希土類−Ａｌ合金及びＢ−Ａｌ合金を異なる時間帯に添加することで，希土類元素及び元素Ｂが全面的に機能することが可能となり，効果を高めることができる。
４．３．希土類−Ａｌ合金及びＢ−Ａｌ合金の供給位置が，均熱炉内で均等に分布することが可能となる。
５．精製（スラグ除去，ガス除去，攪拌及び除滓）
５．１．均熱炉全体で液状アルミニウム合金の成分を均質にするために，該液状アルミニウム合金を，均熱炉の隅部の位置にあるものも含めて５分間攪拌する。
５．２．均熱炉に液状アルミニウム合金が充満した後，液状アルミニウム合金の底部内で吹込みノズルを動かしながら，２．３ｋｇの精製剤（２３％のＮａ3Ａｌ・Ｆ6＋４７％のＫＣｌ＋３０％のＮａＣｌ）の粉末を，高純度窒素ガスで液状アルミニウム合金の底部に３〜５分間吹き込み，ガスによって，含有スラグを該液状アルミニウム合金の表面に沿って均一に上昇させる。浮遊している酸化アルミニウムスラグを炉から完全に除去することで，精製剤がもたらした新たな不純物を，可能な限り減少させることができる。
６．現場で採取した試料の迅速な分析と保持及び熱保存
液状アルミニウム合金のＦｅの含有量がスラグの除去後の要件を満たす場合，液状アルミニウム合金を２０〜４０分間保持する。
７．連続鋳造及び圧延処理の制御
７．１．温度制御
７．１．１．鋳造用取鍋の温度：７２０〜７３０℃
７．１．２．圧延機へ供給される条片の温度：４５０〜４９０℃
７．１．３．アルミニウムロッドの最終圧延温度：約３００℃
７．２．連続鋳造機内の冷却水の制御
鋳造ホイールの外部の水量に対する鋳造ホイールの内部の水量：３：２；
２次冷却水の量は，鋳造された条片の温度にあわせて調節する。
７．３．鋳造機の電圧：６０〜９０Ｖ
７．４．圧延機を通過する電流：２００〜２８０Ａ；圧延機の速度：７．５〜８．５ｍ／分
Reference Example I. Melt casting process Material formulation 5110 kg Si-Fa-Al alloy ingot (containing 0.10% Si and 0.13% Fe), 258 kg Al-Fe alloy (containing 23.2% Fe), 166. 5 kg rare earth- Al alloy (containing 9.8% rare earth element), 10 kg B-Al alloy (containing 3.3% B), and 2.3 kg refining agent (23% Na 3 Al. F 6 + 47% KCl + 30% NaCl)
2. Supplying method In order to distribute the components as evenly as possible during the supply of the material, the Al—Fe alloy is supplied evenly in batches together with the Si—Fa—Al alloy ingot in the hot metal furnace.
3. Heat preservation treatment When a liquid aluminum alloy is poured into a soaking furnace, the temperature of the soaking furnace is controlled at 710 to 750 ° C; when a rare earth-Al alloy and a B-Al alloy are added to the liquid aluminum alloy, the soaking furnace Is raised to 720-760 ° C, but the temperature does not exceed 760 ° C. Here, the increase in temperature is suitable for melting of the rare earth-Al alloy and the B-Al alloy, so that the treatment effect of the rare earth element and the element B can be improved.
4). Rare earth treatment and boride treatment 4.1. One-third of the rare earth-Al alloy is added 30 minutes before the soaking furnace is filled with the liquid aluminum alloy.
4.2. 5 minutes before the soaking furnace is filled with the liquid aluminum alloy, the remaining two thirds of the rare earth-Al alloy and the B-A alloy are added.
By adding the rare earth-Al alloy and the B-Al alloy in different time zones, the rare earth element and the element B can function entirely, and the effect can be enhanced.
4.3. The supply positions of the rare earth-Al alloy and the B-Al alloy can be evenly distributed in the soaking furnace.
5. Refinement (slag removal, gas removal, stirring and removal)
5.1. In order to make the components of the liquid aluminum alloy homogeneous throughout the soaking furnace, the liquid aluminum alloy is stirred for 5 minutes, including those at the corners of the soaking furnace.
5.2. After the soaking furnace is filled with liquid aluminum alloy, 2.3 kg of refining agent (23% Na 3 Al · F 6 + 47% KCl + 30% NaCl) while moving the blowing nozzle in the bottom of the liquid aluminum alloy The powder is blown into the bottom of the liquid aluminum alloy with high-purity nitrogen gas for 3 to 5 minutes, and the contained slag is uniformly raised along the surface of the liquid aluminum alloy by the gas. By completely removing the suspended aluminum oxide slag from the furnace, the new impurities introduced by the refining agent can be reduced as much as possible.
6). If the Fe content of the sample collected on-site is quickly analyzed and maintained and the heat-preserving liquid aluminum alloy meets the requirements after slag removal, the liquid aluminum alloy is held for 20-40 minutes.
7). Control of continuous casting and rolling process 7.1. Temperature control 7.1.1. Casting ladle temperature: 720-730 ° C
7.1.2. Temperature of strip supplied to rolling mill: 450-490 ° C
7.1.3. Final rolling temperature of aluminum rod: about 300 ° C
7.2. Control of cooling water in the continuous casting machine Water volume inside the casting wheel relative to the water volume outside the casting wheel: 3: 2;
The amount of secondary cooling water is adjusted according to the temperature of the cast strip.
7.3. Casting machine voltage: 60-90V
7.4. Current passing through the rolling mill: 200 to 280 A; Speed of the rolling mill: 7.5 to 8.5 m / min
実施例２
Ｉ．溶融鋳造処理
１．材料の配合
５１２５ｋｇのＳｉ−Ｆａ−Ａｌ合金のインゴット（０．１２％のＳｉ及び０．１２％のＦｅを含有），１０７ｋｇのＡｌ−Ｆｅ合金（２１．９％のＦｅを含有），１１８ｋｇの希土類−Ａｌ合金（１０．１％の希土類元素を含有），１４．８ｋｇのＢ−Ａｌ合金（３．０％のＢを含有），及び２．８ｋｇの精製剤（２３％のＮａ3Ａｌ・Ｆ6＋４７％のＫＣｌ＋３０％のＮａＣｌ）
２．供給方法
材料の供給中に，成分をできる限り均等に分配するために，溶銑炉内に，Ｓｉ−Ｆａ−Ａｌ合金のインゴットと共に，Ａｌ−Ｆｅ合金をバッチごとに均等に供給する。
３．熱保存処理
液状アルミニウム合金を均熱炉に流し入れる場合，該均熱炉の温度は７１０〜７５０℃に制御する；希土類−Ａｌ合金及びＢ−Ａｌ合金を液状アルミニウム合金に添加する場合，均熱炉の温度を７２０〜７６０℃に上昇させるが，該温度は７６０℃を越えない。ここで，温度の上昇は希土類−Ａｌ合金及びＢ−Ａｌ合金の融解に好適であり，それにより，希土類元素及び元素Ｂの処理効果を向上させることが可能となる。
４．希土類処理及びホウ化処理
４．１．均熱炉に液状アルミニウム合金が充満する３０分前に，３分の１の希土類−Ａｌ合金を添加する。
４．２．均熱炉に液状アルミニウム合金が充満する５分前に，残りの３分の２の希土類−Ａｌ合金及びＢ−Ａ合金を添加する。
４．３．希土類−Ａｌ合金及びＢ−Ａｌ合金の供給位置が，均熱炉内で均等に分布することが可能となる。
５．精製（スラグ除去，ガス除去，攪拌及び除滓）
５．１．均熱炉全体で液状アルミニウム合金の成分を均質にするために，該液状アルミニウム合金を，均熱炉の隅部の位置にあるものも含めて５分間攪拌する。
５．２．均熱炉に液状アルミニウム合金が充満した後，液状アルミニウム合金の底部内で吹込みノズルを動かしながら，２．８ｋｇの精製剤（２３％のＮａ3Ａｌ・Ｆ6＋４７％のＫＣｌ＋３０％のＮａＣｌ）の粉末を，高純度窒素ガスで液状アルミニウム合金の底部に３〜５分間吹き込み，ガスによって，含有スラグを該液状アルミニウム合金の表面に沿って均一に上昇させる。浮遊している酸化アルミニウムスラグを炉から完全に除去することで，精製剤がもたらした新たな不純物を，可能な限り減少させることができる。
６．現場で採取した試料の迅速な分析と保持及び熱保存
液状アルミニウム合金のＦｅの含有量がスラグの除去後の要件を満たす場合，液状アルミニウム合金を２０〜４０分間保持する。
７．連続鋳造及び圧延処理の制御
７．１．温度制御
７．１．１．鋳造用取鍋の温度：７２０〜７３０℃
７．１．２．圧延機へ供給される条片の温度：４５０〜４９０℃
７．１．３．アルミニウムロッドの最終圧延温度：約３００℃
７．２．連続鋳造機内の冷却水の制御
鋳造ホイールの外部の水量に対する鋳造ホイールの内部の水量：３：２；
２次冷却水の量は，鋳造された条片の温度にあわせて調節する。
７．３．鋳造機の電圧：６０〜９０Ｖ
７．４．圧延機を通過する電流：２００〜２８０Ａ；圧延機の速度：７．５〜８．５ｍ／分
Example 2
I. Melt casting process Material formulation 5125 kg Si-Fa-Al alloy ingot (containing 0.12% Si and 0.12% Fe), 107 kg Al-Fe alloy (containing 21.9% Fe), 118 kg Rare earth- Al alloy (containing 10.1% rare earth element), 14.8 kg B-Al alloy (containing 3.0% B), and 2.8 kg refining agent (23% Na 3 Al. F 6 + 47% KCl + 30% NaCl)
2. Supplying method In order to distribute the components as evenly as possible during the supply of the material, the Al—Fe alloy is supplied evenly in batches together with the Si—Fa—Al alloy ingot in the hot metal furnace.
3. When the heat-preserving liquid aluminum alloy is poured into a soaking furnace, the temperature of the soaking furnace is controlled at 710 to 750 ° C .; when adding rare earth-Al alloy and B-Al alloy to the liquid aluminum alloy, the soaking furnace Is raised to 720-760 ° C, but the temperature does not exceed 760 ° C. Here, the increase in temperature is suitable for melting of the rare earth-Al alloy and the B-Al alloy, so that the treatment effect of the rare earth element and the element B can be improved.
4). Rare earth treatment and boride treatment 4.1. One-third of the rare earth-Al alloy is added 30 minutes before the soaking furnace is filled with the liquid aluminum alloy.
4.2. 5 minutes before the soaking furnace is filled with the liquid aluminum alloy, the remaining two thirds of the rare earth-Al alloy and the B-A alloy are added.
4.3. The supply positions of the rare earth-Al alloy and the B-Al alloy can be evenly distributed in the soaking furnace.
5. Refinement (slag removal, gas removal, stirring and removal)
5.1. In order to make the components of the liquid aluminum alloy homogeneous throughout the soaking furnace, the liquid aluminum alloy is stirred for 5 minutes, including those at the corners of the soaking furnace.
5.2. After the soaking furnace is filled with the liquid aluminum alloy, 2.8 kg of refining agent (23% Na 3 Al · F 6 + 47% KCl + 30% NaCl) while moving the blowing nozzle in the bottom of the liquid aluminum alloy The powder is blown into the bottom of the liquid aluminum alloy with high-purity nitrogen gas for 3 to 5 minutes, and the contained slag is uniformly raised along the surface of the liquid aluminum alloy by the gas. By completely removing the suspended aluminum oxide slag from the furnace, the new impurities introduced by the refining agent can be reduced as much as possible.
6). If the Fe content of the sample collected on-site is quickly analyzed and maintained and the heat-preserving liquid aluminum alloy meets the requirements after slag removal, the liquid aluminum alloy is held for 20-40 minutes.
7). Control of continuous casting and rolling process 7.1. Temperature control 7.1.1. Casting ladle temperature: 720-730 ° C
7.1.2. Temperature of strip supplied to rolling mill: 450-490 ° C
7.1.3. Final rolling temperature of aluminum rod: about 300 ° C
7.2. Control of cooling water in the continuous casting machine Water volume inside the casting wheel relative to the water volume outside the casting wheel: 3: 2;
The amount of secondary cooling water is adjusted according to the temperature of the cast strip.
7.3. Casting machine voltage: 60-90V
7.4. Current passing through the rolling mill: 200 to 280 A; Speed of the rolling mill: 7.5 to 8.5 m / min
実施例３
Ｉ．溶融鋳造処理
１．材料の配合
５００５ｋｇのＳｉ−Ｆａ−Ａｌ合金のインゴット（０．０８％のＳｉ及び０．１３％のＦｅを含有），１８２ｋｇのＡｌ−Ｆｅ合金（２１％のＦｅを含有），９０．５ｋｇの希土類−Ａｌ合金（９．８％の希土類元素を含有），３０ｋｇのＢ−Ａｌ合金（３．５％のＢを含有），及び２．０ｋｇの精製剤（２３％のＮａ3Ａｌ・Ｆ6＋４７％のＫＣｌ＋３０％のＮａＣｌ）
２．供給方法
材料の供給中に，成分をできる限り均等に分配するために，溶銑炉内に，Ｓｉ−Ｆａ−Ａｌ合金のインゴットと共に，Ａｌ−Ｆｅ合金をバッチごとに均等に供給する。
３．熱保存処理
液状アルミニウム合金を均熱炉に流し入れる場合，該均熱炉の温度は７１０〜７５０℃に制御する；希土類−Ａｌ合金及びＢ−Ａｌ合金を液状アルミニウム合金に添加する場合，均熱炉の温度を７２０〜７６０℃に上昇させるが，該温度は７６０℃を越えない。ここで，温度の上昇は希土類−Ａｌ合金及びＢ−Ａｌ合金の融解に好適であり，それにより，希土類元素及び元素Ｂの処理効果を向上させることが可能となる。
４．希土類処理及びホウ化処理
４．１．均熱炉に液状アルミニウム合金が充満する３０分前に，３分の１の希土類−Ａｌ合金を添加する。
４．２．均熱炉に液状アルミニウム合金が充満する５分前に，残りの３分の２の希土類−Ａｌ合金及びＢ−Ａ合金を添加する。
４．３．希土類−Ａｌ合金及びＢ−Ａｌ合金の供給位置が，均熱炉内で均等に分布することが可能となる。
５．精製（スラグ除去，ガス除去，攪拌及び除滓）
５．１．均熱炉全体で液状アルミニウム合金の成分を均質にするために，該液状アルミニウム合金を，均熱炉の隅部の位置にあるものも含めて５分間攪拌する。
５．２．均熱炉に液状アルミニウム合金が充満した後，液状アルミニウム合金の底部内で吹込みノズルを動かしながら，２．０ｋｇの精製剤（２３％のＮａ3Ａｌ・Ｆ6＋４７％のＫＣｌ＋３０％のＮａＣｌ）の粉末を，高純度窒素ガスで液状アルミニウム合金の底部に３〜５分間吹き込み，ガスによって，含有スラグを該液状アルミニウム合金の表面に沿って均一に上昇させる。浮遊している酸化アルミニウムスラグを炉から完全に除去することで，精製剤がもたらした新たな不純物を，可能な限り減少させることができる。
６．現場で採取した試料の迅速な分析と保持及び熱保存
液状アルミニウム合金のＦｅの含有量がスラグの除去後の要件を満たす場合，液状アルミニウム合金を２０〜４０分間保持する。
７．連続鋳造及び圧延処理の制御
７．１．温度制御
７．１．１．鋳造用取鍋の温度：７２０〜７３０℃
７．１．２．圧延機へ供給される条片の温度：４５０〜４９０℃
７．１．３ ．アルミニウムロッドの最終圧延温度：約３００℃
７．２．連続鋳造機内の冷却水の制御
鋳造ホイールの外部の水量に対する鋳造ホイールの内部の水量：３：２；
２次冷却水の量は，鋳造された条片の温度にあわせて調節する。
７．３．鋳造機の電圧：６０〜９０Ｖ
７．４．圧延機を通過する電流：２００〜２８０Ａ；圧延機の速度：７．５〜８．５ｍ／分
Example 3
I. Melt casting process Material mix 5005 kg Si-Fa-Al alloy ingot (containing 0.08% Si and 0.13% Fe), 182 kg Al-Fe alloy (containing 21% Fe), 90.5 kg Rare earth- Al alloy (containing 9.8% rare earth element), 30 kg B-Al alloy (containing 3.5% B), and 2.0 kg refining agent (23% Na 3 Al · F 6 + 47% KCl + 30% NaCl)
2. Supplying method In order to distribute the components as evenly as possible during the supply of the material, the Al—Fe alloy is supplied evenly in batches together with the Si—Fa—Al alloy ingot in the hot metal furnace.
3. Heat preservation treatment When a liquid aluminum alloy is poured into a soaking furnace, the temperature of the soaking furnace is controlled at 710 to 750 ° C; when a rare earth-Al alloy and a B-Al alloy are added to the liquid aluminum alloy, the soaking furnace Is raised to 720-760 ° C, but the temperature does not exceed 760 ° C. Here, the increase in temperature is suitable for melting of the rare earth-Al alloy and the B-Al alloy, so that the treatment effect of the rare earth element and the element B can be improved.
4). Rare earth treatment and boride treatment 4.1. One-third of the rare earth-Al alloy is added 30 minutes before the soaking furnace is filled with the liquid aluminum alloy.
4.2. 5 minutes before the soaking furnace is filled with the liquid aluminum alloy, the remaining two thirds of the rare earth-Al alloy and the B-A alloy are added.
4.3. The supply positions of the rare earth-Al alloy and the B-Al alloy can be evenly distributed in the soaking furnace.
5. Refinement (slag removal, gas removal, stirring and removal)
5.1. In order to make the components of the liquid aluminum alloy homogeneous throughout the soaking furnace, the liquid aluminum alloy is stirred for 5 minutes, including those at the corners of the soaking furnace.
5.2. After the soaking furnace is filled with the liquid aluminum alloy, 2.0 kg of refining agent (23% Na 3 Al · F 6 + 47% KCl + 30% NaCl) while moving the blowing nozzle in the bottom of the liquid aluminum alloy The powder is blown into the bottom of the liquid aluminum alloy with high-purity nitrogen gas for 3 to 5 minutes, and the contained slag is uniformly raised along the surface of the liquid aluminum alloy by the gas. By completely removing the suspended aluminum oxide slag from the furnace, the new impurities introduced by the refining agent can be reduced as much as possible.
6). If the Fe content of the sample collected on-site is quickly analyzed and maintained and the heat-preserving liquid aluminum alloy meets the requirements after slag removal, the liquid aluminum alloy is held for 20-40 minutes.
7). Control of continuous casting and rolling process 7.1. Temperature control 7.1.1. Casting ladle temperature: 720-730 ° C
7.1.2. Temperature of strip supplied to rolling mill: 450-490 ° C
7.1.3. Final rolling temperature of aluminum rod: about 300 ° C
7.2. Control of cooling water in the continuous casting machine Water volume inside the casting wheel relative to the water volume outside the casting wheel: 3: 2;
The amount of secondary cooling water is adjusted according to the temperature of the cast strip.
7.3. Casting machine voltage: 60-90V
7.4. Current passing through the rolling mill: 200 to 280 A; Speed of the rolling mill: 7.5 to 8.5 m / min
Claims (9)
０．３０〜０．８０％のＦｅと，
０．０３〜０．１０％のＳｉと，
０．０１〜０．３０％のＣｅ及びＬａから成る希土類元素と，
残存部分がＡｌ及び不可避的不純物と
から成るケーブル用の高い延伸性を有するアルミニウム合金材料。 The following ingredients measured in weight percent;
0.30 to 0.80 % Fe,
0.03-0.10% Si,
A rare-earth element consisting of from 0.01 to 0.30% of Ce and La,
The remaining part is Al and inevitable impurities
An aluminum alloy material having high extensibility for a cable comprising:
最初に９２〜９８重量部（ｐｂｗ）のＳｉ−Ｆｅ−Ａｌ合金と０．７３〜５．２６ｐｂｗのＡｌ―Ｆｅ合金を添加し，７１０〜７５０℃に融解状態まで加熱し；次に７２０〜７６０℃に加熱し，１〜３ｐｂｗの希土類―Ａｌ合金及び０．１７〜０．６７ｐｂｗのＢ−Ａｌ合金を添加し，ここでは，前記希土類―Ａｌ合金はＡｌとＣｅ及びＬａから成る希土類元素との合金であり；次に，０．０４〜０．０６ｐｂｗの精製剤を添加し，８〜２０分間精製し；次に前記温度で２０〜４０分間保持し，その後，鋳造する工程と，
２）半焼鈍処理
得られたアルミニウム合金を２８０〜３８０℃で４〜１０時間保持し，その後，取り出して，周囲温度まで自然に冷却する工程と
を含む請求項１記載のケーブル用の高い延伸性を有するアルミニウム合金材料の製造方法。 1) Melt casting First, 92-98 parts by weight (pbw) of Si-Fe-Al alloy and 0 . It was added 73~5.26 pbw Al-F e alloy of, and heated to a molten state to seven hundred ten to seven hundred and fifty ° C.; then heated to seven hundred and twenty to seven hundred sixty ° C., rare earth 1～3Pbw -Al alloy and 0.17 It was added ~0.67pbw of B-Al alloy, wherein the said rare earth -Al alloy is an alloy of rare-earth element consisting of Al and Ce and La; Next, seminal of 0.04~0.06pbw Adding the formulation and purifying for 8-20 minutes; then holding at said temperature for 20-40 minutes and then casting;
2) Semi-annealing treatment The obtained aluminum alloy is held at 280 to 380 ° C. for 4 to 10 hours, and then taken out and naturally cooled to the ambient temperature. The manufacturing method of the aluminum alloy material which has this.
Applications Claiming Priority (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN2009101166357A CN101525709B (en) | 2009-04-24 | 2009-04-24 | High-elongation aluminum alloy material and preparation method thereof |
| CN200910116635.7 | 2009-04-24 | ||
| PCT/CN2010/071654 WO2010121517A1 (en) | 2009-04-24 | 2010-04-09 | High-elongation rate aluminum alloy material for cable and preparation method thereof |
Publications (2)
| Publication Number | Publication Date |
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| JP2012524837A JP2012524837A (en) | 2012-10-18 |
| JP2012524837A5 true JP2012524837A5 (en) | 2014-05-01 |
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| Application Number | Title | Priority Date | Filing Date |
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| JP2012506317A Pending JP2012524837A (en) | 2009-04-24 | 2010-04-09 | Aluminum alloy material having high stretchability for cable and method for producing the same |
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| Country | Link |
|---|---|
| US (1) | US20120211130A1 (en) |
| EP (1) | EP2468907A4 (en) |
| JP (1) | JP2012524837A (en) |
| CN (1) | CN101525709B (en) |
| AU (1) | AU2010239014B2 (en) |
| CA (1) | CA2773050A1 (en) |
| RU (1) | RU2550063C2 (en) |
| WO (1) | WO2010121517A1 (en) |
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-
2009
- 2009-04-24 CN CN2009101166357A patent/CN101525709B/en active Active
-
2010
- 2010-04-09 RU RU2011147346/02A patent/RU2550063C2/en active
- 2010-04-09 EP EP10766607.5A patent/EP2468907A4/en not_active Withdrawn
- 2010-04-09 AU AU2010239014A patent/AU2010239014B2/en active Active
- 2010-04-09 JP JP2012506317A patent/JP2012524837A/en active Pending
- 2010-04-09 CA CA2773050A patent/CA2773050A1/en not_active Abandoned
- 2010-04-09 WO PCT/CN2010/071654 patent/WO2010121517A1/en active Application Filing
- 2010-04-09 US US13/395,423 patent/US20120211130A1/en not_active Abandoned
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