JP7665222B2 - High strength aluminum alloy general-purpose welding wire and its manufacturing method - Google Patents
High strength aluminum alloy general-purpose welding wire and its manufacturing method Download PDFInfo
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K35/00—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting
- B23K35/02—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by mechanical features, e.g. shape
- B23K35/0255—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by mechanical features, e.g. shape for use in welding
- B23K35/0261—Rods, electrodes or wires
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K35/00—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting
- B23K35/22—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by the composition or nature of the material
- B23K35/24—Selection of soldering or welding materials proper
- B23K35/28—Selection of soldering or welding materials proper with the principal constituent melting at less than 950°C
- B23K35/286—Al as the principal constituent
- B23K35/288—Al as the principal constituent with Sn or Zn
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K35/00—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting
- B23K35/40—Making wire or rods for soldering or welding
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Description
本発明は、高強度アルミニウム合金の溶接の技術分野に関し、具体的には、高強度アルミニウム合金の汎用溶接ワイヤ及びその製造方法に関する。 The present invention relates to the technical field of welding high-strength aluminum alloys, and more specifically to a general-purpose welding wire for high-strength aluminum alloys and a method for manufacturing the same.
７０５０、７０５５、７０７５、７４７５及び７０８５などの７ＸＸＸシリーズのアルミニウム合金は、Ａｌ－Ｚｎ－Ｍｇ－Ｃｕ系超硬アルミニウム合金に属し、比強度が高く、航空宇宙、軌道交通などの分野で広く使用される。Ａｌ－Ｚｎ－Ｍｇ－Ｃｕ系アルミニウム合金は、強度が高いが塑性が低く、従来の伸線加工法によって溶接ワイヤの加工を順調に行うことができず、また、溶接時に溶接継手に熱割れや応力腐食割れが発生しやすいため、Ａｌ－Ｚｎ－Ｍｇ－Ｃｕアルミニウム合金の溶接が困難で、溶接性が低くなるという問題をもたらす。現在、Ａｌ－Ｚｎ－Ｍｇ－Ｃｕ系高強度アルミニウム合金の溶接には、溶接性能に優れたバルクのワイヤの供給が不足しており、特にほとんどの高強度アルミニウム合金の溶接に適した汎用ワイヤが不足している。 7XXX series aluminum alloys, such as 7050, 7055, 7075, 7475 and 7085, belong to Al-Zn-Mg-Cu based superhard aluminum alloys, and have high specific strength and are widely used in aerospace, rail transportation and other fields. Al-Zn-Mg-Cu based aluminum alloys have high strength but low plasticity, and cannot be smoothly processed into welding wire by conventional wire drawing methods. In addition, heat cracking and stress corrosion cracking are easily generated in the welded joint during welding, which makes welding of Al-Zn-Mg-Cu aluminum alloys difficult and leads to poor weldability. Currently, there is a shortage of bulk wires with excellent welding performance for welding Al-Zn-Mg-Cu based high-strength aluminum alloys, and in particular, there is a shortage of general-purpose wires suitable for welding most high-strength aluminum alloys.
上記の技術的問題に対して、第ＣＮ１１２８３１７３５Ａ号の中国特許出願は、高強度アルミニウム合金ワイヤ／ストリップの製造方法を開示し、それは、射出成形によってビレットを製造した後、半固体状態で押出し及び熱間押出し、様々な仕様のＡｌ－Ｚｎ－Ｍｇ－Ｃｕ高強度アルミニウム合金ワイヤを得る。しかし、この方法で製造されたワイヤは、対応する特定のグレードのアルミニウム合金にしか溶接できず、ほとんどのアルミニウム合金、特に７ＸＸＸシリーズの高強度アルミニウム合金に対しては汎用性がなく、使用が不便であり、高強度アルミニウム合金、特に超高強度アルミニウム合金の応用を制限する。 In response to the above technical problems, Chinese patent application No. CN112831735A discloses a method for producing high-strength aluminum alloy wire/strip, which involves producing a billet by injection molding, followed by extrusion and hot extrusion in a semi-solid state to obtain Al-Zn-Mg-Cu high-strength aluminum alloy wires of various specifications. However, the wire produced by this method can only be welded to a corresponding specific grade of aluminum alloy, which is not versatile for most aluminum alloys, especially 7XXX series high-strength aluminum alloys, and is inconvenient to use, limiting the application of high-strength aluminum alloys, especially ultra-high-strength aluminum alloys.
現在、中国の研究状況にもいくつかの進歩があり、Ｓｃ又はＺｒ－ＳｃがＡｌ－Ｍｇ－Ｓｃ合金溶接継手の微細構造及び特性への影響を研究する人がおり、また、従来のＥＲ５３５６溶接ワイヤ及びＳｃ、Ｚｒ、Ｅｒを加えたＥＲ５３５６溶接ワイヤを使用し、７Ａ５２アルミニウム合金に対してタングステン電極不活性ガスシールド溶接を行い、Ｓｃ、Ｚｒ、Ｅｒが溶接継手の機械的特性への影響を研究する人もいる。しかし、これらは溶接ワイヤ原料の大量生産の問題を解決しておらず、価格が高いため、Ａｌ－Ｚｎ－Ｍｇ－Ｃｕ高強度アルミニウム合金の構造部品の加工及び応用を大幅に制限する。 At present, there has been some progress in the research situation in China. Some people have studied the effects of Sc or Zr-Sc on the microstructure and properties of Al-Mg-Sc alloy welded joints, and some people have used conventional ER5356 welding wire and ER5356 welding wire with Sc, Zr, and Er added to perform tungsten electrode inert gas shielded welding of 7A52 aluminum alloy to study the effects of Sc, Zr, and Er on the mechanical properties of the welded joints. However, these have not solved the problem of mass production of welding wire raw materials, and the high price greatly restricts the processing and application of Al-Zn-Mg-Cu high-strength aluminum alloy structural parts.
従来の溶接ワイヤは、ほとんどのＡｌ－Ｚｎ－Ｍｇ－Ｃｕ系高強度アルミニウム合金に対して汎用性がなく大量生産が困難であるという技術的問題を有する。本発明は、前記技術的問題を解決するために、高強度アルミニウム合金の汎用溶接ワイヤ及びその製造方法を提供する。本発明の方法によって得られた溶接ワイヤは、ほとんどのＡｌ－Ｚｎ－Ｍｇ－Ｃｕ系高強度アルミニウム合金の構造部品に対して優れた溶接性能を有し、大量生産が容易である。 Conventional welding wires have the technical problem that they are not versatile for most Al-Zn-Mg-Cu high-strength aluminum alloys and are difficult to mass-produce. In order to solve the above technical problem, the present invention provides a versatile welding wire for high-strength aluminum alloys and a manufacturing method thereof. The welding wire obtained by the method of the present invention has excellent welding performance for most structural parts made of Al-Zn-Mg-Cu high-strength aluminum alloys and is easy to mass-produce.
上記の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用いる。 To achieve the above objectives, the present invention uses the following technical solutions:
高強度アルミニウム合金の汎用溶接ワイヤの製造方法は、
Ａｌ－Ｚｎ－Ｍｇ－Ｃｕ系アルミニウム合金とＢ及びＺｒを混合した後に合金を溶融し、次に、射出成形によってビレットを得て、前記ビレットを半固体状態で据え込み加工し、インゴットを形成し、前記インゴットを熱間押出して棒材を得てコイル状にするステップ（１）と、
コイル状の前記棒材を焼戻しし、次に、必要な溶接ワイヤの直径まで連続して複数パスの圧延・伸線加工を行い、サイジング、丸め加工、多結晶ダイによる艶出し、微細研磨、洗浄及び乾燥を順次行い、高強度アルミニウム合金の汎用溶接ワイヤを得るステップ（２）とを含む。焼戻しした後、必要な寸法まで連続して圧延すると、圧延工程における焼戻し工程を省くことができ、また、割れ目が少なくて破断しない。
The manufacturing method of high strength aluminum alloy general-purpose welding wire is as follows:
(1) mixing an Al-Zn-Mg-Cu based aluminum alloy with B and Zr, melting the alloy, then obtaining a billet by injection molding, upsetting the billet in a semi-solid state to form an ingot, and hot extruding the ingot to obtain a rod and coil it;
and (2) tempering the coiled rod, and then continuously rolling and drawing the rod in multiple passes to the required welding wire diameter, followed by sizing, rounding, polishing with a polycrystalline die, fine polishing, cleaning and drying to obtain a high-strength aluminum alloy general-purpose welding wire. If the rod is continuously rolled to the required dimensions after tempering, the tempering step in the rolling process can be omitted, and there is little cracking and no breakage.
更に、前記Ａｌ－Ｚｎ－Ｍｇ－Ｃｕ系アルミニウム合金の成分は、重量百分率で、５～８％のＺｎ、１．５～５％のＭｇ、及び１～３％のＣｕを含み、残部がＡｌである。 Furthermore, the composition of the Al-Zn-Mg-Cu-based aluminum alloy includes, by weight percentage, 5-8% Zn, 1.5-5% Mg, and 1-3% Cu, with the remainder being Al.
更に、前記Ａｌ－Ｚｎ－Ｍｇ－Ｃｕ系アルミニウム合金の成分は、重量百分率で、７～８％のＺｎ、２～３％のＭｇ、及び１．５～２．５％のＣｕを含み、残部がＡｌである。 Furthermore, the composition of the Al-Zn-Mg-Cu-based aluminum alloy is, by weight percentage, 7-8% Zn, 2-3% Mg, 1.5-2.5% Cu, and the remainder is Al.
更に、Ｂ及びＺｒの添加量はそれぞれ前記Ａｌ－Ｚｎ－Ｍｇ－Ｃｕ系アルミニウム合金の重量の０．１～１重量％である。 Furthermore, the amount of B and Zr added is 0.1 to 1 weight percent of the weight of the Al-Zn-Mg-Cu-based aluminum alloy.
更に、Ｂ及びＺｒの添加量はそれぞれ前記Ａｌ－Ｚｎ－Ｍｇ－Ｃｕ系アルミニウム合金の重量の０．１～０．５重量％である。微量元素Ｂ及びＺｒの合計量が１重量％を超えると、材料はより脆くなる。 Furthermore, the amount of B and Zr added is 0.1-0.5 wt% of the weight of the Al-Zn-Mg-Cu-based aluminum alloy. If the total amount of the trace elements B and Zr exceeds 1 wt%, the material becomes more brittle.
更に、ステップ（１）における前記半固体状態での据え込み加工は、４６０～５７５℃で前記ビレットを据え込み加工することであり、ステップ（２）における前記焼戻しは、２００～３００℃の温度で少なくとも１０時間保温することである。 Furthermore, the upsetting in the semi-solid state in step (1) involves upsetting the billet at 460 to 575°C, and the tempering in step (2) involves maintaining the temperature at 200 to 300°C for at least 10 hours.
更に、ステップ（１）における前記熱間押出は、３８０～４８０℃の温度で、直径１５０～３００ｍｍの前記インゴットを直径５～１０ｍｍの棒材に熱間押出することである。 Furthermore, the hot extrusion in step (1) involves hot extruding the ingot having a diameter of 150 to 300 mm into a rod having a diameter of 5 to 10 mm at a temperature of 380 to 480°C.
更に、ステップ（２）における前記圧延・伸線加工は、横型ローラーダイス伸線機で連続して少なくとも５パスの伸線を行うことであり、各パスの伸線面の圧縮率が６～８％であり、直径０．８～１．６ｍｍまで伸線を行う。 Furthermore, the rolling and drawing process in step (2) involves drawing at least five passes of wire continuously using a horizontal roller die wire drawing machine, with the compression ratio of the wire drawing surface in each pass being 6-8%, and drawing to a diameter of 0.8-1.6 mm.
本発明の別態様は、上記の製造方法によって得られた高強度アルミニウム合金の汎用溶接ワイヤを提供し、前記溶接ワイヤは、Ａｌ－Ｚｎ－Ｍｇ－Ｃｕ系アルミニウム合金を母材として使用し、前記母材の重量の０．１～１％のＢ及び母材の重量の０．１～１％のＺｒを加えることによって製造され、Ａｌ－Ｚｎ－Ｍｇ－Ｃｕ系アルミニウム合金の溶接には、汎用性があり、特に、７０５０、７０５５、７０７５、７４７５、７０８５などのＡｌ－Ｚｎ－Ｍｇ－Ｃｕ超硬アルミニウム合金の溶接に適用する。 Another aspect of the present invention provides a general-purpose welding wire of high-strength aluminum alloy obtained by the above manufacturing method, the welding wire being manufactured by using an Al-Zn-Mg-Cu aluminum alloy as a base material and adding 0.1 to 1% of B and 0.1 to 1% of Zr by weight of the base material, and the welding wire is versatile for welding Al-Zn-Mg-Cu aluminum alloys, and is particularly applicable to welding Al-Zn-Mg-Cu superhard aluminum alloys such as 7050, 7055, 7075, 7475, and 7085.
有益な技術的効果は、以下のとおりである。本発明では、微量元素Ｂ及びＺｒをＡｌ－Ｚｎ－Ｍｇ－Ｃｕ系アルミニウム合金に加え、溶融した後、射出成形により、微細な粒子と均一な成分のある母材を得て、Ａｌ－Ｚｎ－Ｍｇ－Ｃｕ高強度アルミニウム合金のビレットは、溶接及び凝固中に微細な結晶粒を保持できる微量元素Ｂ及びＺｒを含有し、半固体状態で据え込み加工することにより、射出成形で形成された層状微細構造を除去し、ビレットは緻密になり、熱間押出、伸線を行った後に得られたワイヤは、結晶粒が細かく緻密で、微細構造が均一で、結晶粒界が明瞭で析出物がなく、層状微細構造がなく、優れた機械的特性、構造的特性、溶接性能を有する。７ＸＸＸシリーズの高強度アルミニウム合金の溶接には、汎用性があり、７ＸＸＸシリーズの高強度アルミニウム合金溶接用の高品質の原料を提供でき、広い高強度アルミニウム合金の溶接のプロセスウィンドウを得ることができる。 The beneficial technical effects are as follows: In the present invention, trace elements B and Zr are added to the Al-Zn-Mg-Cu aluminum alloy, and after melting, a base material with fine grains and uniform components is obtained by injection molding. The billet of Al-Zn-Mg-Cu high-strength aluminum alloy contains trace elements B and Zr, which can maintain fine grains during welding and solidification. By upsetting in the semi-solid state, the lamellar microstructure formed by injection molding is removed, and the billet becomes dense. After hot extrusion and wire drawing, the wire obtained has fine and dense grains, uniform microstructure, clear grain boundary, no precipitates, no lamellar microstructure, and has excellent mechanical properties, structural properties and welding performance. The welding of 7XXX series high-strength aluminum alloys is versatile, and can provide high-quality raw materials for welding 7XXX series high-strength aluminum alloys, and a wide process window for welding high-strength aluminum alloys can be obtained.
具体的なプロセスは、表１で示される。
The specific process is shown in Table 1.
以下、本発明の実施例及び図面を参照し、本発明の実施例における技術的解決手段を明確、完全に説明し、明らかに、説明された実施例は、本発明の全てではないが一部の実施例に過ぎない。少なくとも１つの例示的な実施例に関する以下の説明は、本質的に単に例示的なものであり、本発明及びその応用又は用途を限定するものとして解釈されることではない。本発明における実施例に基づき、創造的な作業なしに当業者によって得られる他の全ての実施例は、本発明の保護範囲に属する。 The following clearly and completely describes the technical solutions in the embodiments of the present invention with reference to the embodiments and drawings of the present invention, and obviously, the described embodiments are only some, but not all, embodiments of the present invention. The following description of at least one exemplary embodiment is merely exemplary in nature and should not be construed as limiting the present invention and its application or uses. All other embodiments obtained by those skilled in the art without creative work based on the embodiments of the present invention fall within the protection scope of the present invention.
特に明記されない限り、これらの実施例における数値は、本発明の範囲を限定するものではない。関連分野の当業者に知られている技術および方法については詳細に説明しない場合があるが、適切な状況下では、これらの技術及び方法は本明細書の一部とみなされるべきである。本明細書に示されて議論される全ての例において、特定の値は例示のみとして解釈されるべきであり、限定として解釈されるべきではない。従って、例示的な実施例の他の例は、異なる値を有してもよい。 Unless otherwise specified, the numerical values in these examples are not intended to limit the scope of the invention. Techniques and methods known to those of skill in the relevant art may not be described in detail, but under appropriate circumstances, these techniques and methods should be considered part of this specification. In all examples shown and discussed herein, the specific values should be construed as illustrative only and not limiting. Thus, other examples of the illustrative embodiments may have different values.
以下の実施例で特定の条件を示さない実験方法は、通常、国家基準に従って測定されるが、対応する国家基準がない場合、一般的な国際基準又は関連企業が提案した基準要件に従って実行される。特に明記されない限り、全ての部数は重量部であり、全ての百分率は重量百分率である。 In the following examples, the experimental methods without specific conditions are usually measured according to national standards, but in the absence of corresponding national standards, they are carried out according to general international standards or standard requirements proposed by relevant enterprises. Unless otherwise specified, all parts are parts by weight, and all percentages are percentages by weight.
（実施例１）
高強度アルミニウム合金の汎用溶接ワイヤの製造方法は、
Ａｌ－Ｚｎ－Ｍｇ－Ｃｕアルミニウム合金、Ｂ単体及びＺｒ単体を準備し、均一に混合した後、合金を溶融し、次に、射出成形によって直径２２０ｍｍのビレットを得るステップ（１）であって、
Ａｌ－Ｚｎ－Ｍｇ－Ｃｕアルミニウム合金の成分は、重量百分率で、７．８％のＺｎ、２．３％のＭｇ、及び２％のＣｕを含み、残部がＡｌであり、Ａｌ－７．８Ｚｎ－２．３Ｍｇ－２Ｃｕアルミニウム合金を記し、
Ｂ単体の添加量は、前記Ａｌ－７．８Ｚｎ－２．３Ｍｇ－２Ｃｕアルミニウム合金の重量の０．１％であり、Ｚｒ単体の添加量は、前記Ａｌ－７．８Ｚｎ－２．３Ｍｇ－２Ｃｕアルミニウム合金の重量の０．１％であり、
前記ビレットを４６０℃で半固体状態で据え込み加工し、直径１７８ｍｍのインゴットを形成し、前記インゴットを３８０℃で熱間押出し、数本の直径５．８ｍｍの棒材を得て、コイル状にするステップ（１）と、
コイル状の前記棒材を真空焼戻し炉に入れ、３００℃で１０時間焼戻しして保温し、炉で冷却した後、横型ローラーダイス伸線機に入れ、必要なワイヤ完成品の直径まで連続して複数パスの圧延・伸線加工を行うステップ（２）であって、各パスの伸線面の圧縮率が６～８％であり、得られた溶接ワイヤの直径が０．８～１．６ｍｍであり、次に、順にサイジングダイでサイジングして丸め加工し、多結晶ダイで艶出しし、研磨ダイで微細研磨し、洗浄して乾燥した後、高強度アルミニウム合金の汎用溶接ワイヤを得るステップ（２）とを含む。
Example 1
The manufacturing method of high strength aluminum alloy general-purpose welding wire is as follows:
Step (1) of preparing an Al-Zn-Mg-Cu aluminum alloy, an elemental B, and an elemental Zr, mixing them uniformly, melting the alloy, and then obtaining a billet having a diameter of 220 mm by injection molding;
The composition of the Al-Zn-Mg-Cu aluminum alloy is, by weight percentage, 7.8% Zn, 2.3% Mg, and 2% Cu, with the balance being Al, and is designated as Al-7.8Zn-2.3Mg-2Cu aluminum alloy;
the amount of B added is 0.1% by weight of the Al-7.8Zn-2.3Mg-2Cu aluminum alloy, and the amount of Zr added is 0.1% by weight of the Al-7.8Zn-2.3Mg-2Cu aluminum alloy;
(1) upsetting the billet in a semi-solid state at 460°C to form an ingot of 178 mm diameter, and hot extruding the ingot at 380°C to obtain several bars of 5.8 mm diameter and coiling the bars;
and (2) placing the coiled rod in a vacuum tempering furnace, tempering and warming at 300°C for 10 hours, cooling in the furnace, and then placing it in a horizontal roller die wire drawing machine to perform multiple passes of rolling and drawing continuously to a required diameter of the finished wire, in which the compression ratio of the drawn surface in each pass is 6-8%, and the diameter of the resulting welding wire is 0.8-1.6 mm. Then, the wire is sized and rounded in a sizing die, polished in a polycrystalline die, finely ground in a polishing die, washed and dried, to obtain a high-strength aluminum alloy general-purpose welding wire.
（実施例２）
本実施例の高強度アルミニウム合金の汎用溶接ワイヤの製造プロセスは、実施例１と同じであるが、その違いは、Ｂ単体の添加量が前記Ａｌ－７．８Ｚｎ－２．３Ｍｇ－２Ｃｕアルミニウム合金の重量の０．２％、Ｚｒ単体の添加量が前記Ａｌ－７．８Ｚｎ－２．３Ｍｇ－２Ｃｕアルミニウム合金の重量の０．５％である。
Example 2
The manufacturing process of the general-purpose welding wire of the high strength aluminum alloy of this embodiment is the same as that of Example 1, except that the amount of B added is 0.2% of the weight of the Al-7.8Zn-2.3Mg-2Cu aluminum alloy, and the amount of Zr added is 0.5% of the weight of the Al-7.8Zn-2.3Mg-2Cu aluminum alloy.
（実施例３）
本実施例の高強度アルミニウム合金の汎用溶接ワイヤの製造プロセスは、実施例１と同じであるが、その違いは、Ｂ単体の添加量が前記Ａｌ－７．８Ｚｎ－２．３Ｍｇ－２Ｃｕアルミニウム合金の重量の０．２％、Ｚｒ単体の添加量が前記Ａｌ－７．８Ｚｎ－２．３Ｍｇ－２Ｃｕアルミニウム合金の重量の０．３％である。本実施例の溶接ワイヤの仕様は、φ１．２ｍｍである。
Example 3
The manufacturing process of the general-purpose welding wire of the high strength aluminum alloy of this embodiment is the same as that of Example 1, except that the amount of B added is 0.2% of the weight of the Al-7.8Zn-2.3Mg-2Cu aluminum alloy, and the amount of Zr added is 0.3% of the weight of the Al-7.8Zn-2.3Mg-2Cu aluminum alloy. The specification of the welding wire of this embodiment is φ1.2 mm.
（実施例４）
本実施例の高強度アルミニウム合金の汎用溶接ワイヤの製造プロセスは、実施例１と同じであるが、その違いは、Ｂ単体の添加量が前記Ａｌ－７．８Ｚｎ－２．３Ｍｇ－２Ｃｕアルミニウム合金の重量の０．４％、Ｚｒ単体の添加量が前記Ａｌ－７．８Ｚｎ－２．３Ｍｇ－２Ｃｕアルミニウム合金の重量の０．４％である。
Example 4
The manufacturing process of the general-purpose welding wire of the high strength aluminum alloy of this embodiment is the same as that of Example 1, but the difference is that the amount of added B alone is 0.4% of the weight of the Al-7.8Zn-2.3Mg-2Cu aluminum alloy, and the amount of added Zr alone is 0.4% of the weight of the Al-7.8Zn-2.3Mg-2Cu aluminum alloy.
（比較例１）
本比較例の高強度アルミニウム合金の汎用溶接ワイヤの製造プロセスは、実施例３と同じであるが、その違いは、Ｂ及びＺｒを加えることである。
(Comparative Example 1)
The manufacturing process of the general-purpose welding wire of the high-strength aluminum alloy of this comparative example is the same as that of Example 3, except that B and Zr are added.
上記の実施例及び比較例における溶接ワイヤの機械的特性は、表２で示される。
（備考：溶接ワイヤの仕様は直径１．２ｍｍである）
The mechanical properties of the welding wires in the above examples and comparative examples are shown in Table 2.
(Note: The welding wire specification is 1.2 mm in diameter.)
上記の各実施例及び比較例によって製造された溶接ワイヤを使用し、様々なグレードの７ＸＸＸシリーズのアルミニウム合金の溶接プロセスを試験する。ＥＳＡＢ社製のＴＩＧ ４３００ｉ ＡＣ／ＤＣインバータＡＣ／ＤＣアルゴンアーク溶接機を選択し、ワイヤ送給機は、ＷＦ－００７Ａ多機能自動アルゴンアークワイヤ送給機、直径は１．２ｍｍ、電流は、変数パラメータであり、他のパラメータは、２０Ｖの電圧、３．２ｍｍのアーク長さ、３０°のワイヤ送給角度、１４０ｃｍ／分間のワイヤ送給速度、３ｍｍ／秒間の溶接速度、１０Ｌ／分間のアルゴン流の量である。各実施例及び比較例によって製造された溶接ワイヤを使用して７ＸＸＸシリーズの高強度アルミニウム合金の汎用溶接ワイヤ（７０５０、７０５５、７０７５）の母材を溶接し、次に、Ｔ６熱処理を行い、又は熱処理を行わず、試験サンプルを得て、ＧＢ／Ｔ２２８．１－２０１０ 金属材料引張試験パート１の室温引張法に従って、機械的特性の試験を行い、溶接部分の室温引張機械的特性を試験し、熱処理サンプルの各グループについて、２つの同じサンプルを配置し、その平均値をとる。試験結果は表４で示される。 The welding wires manufactured according to the above examples and comparative examples are used to test the welding process of various grades of 7XXX series aluminum alloys. An ESAB TIG 4300i AC/DC inverter AC/DC argon arc welding machine is selected, the wire feeder is a WF-007A multi-function automatic argon arc wire feeder, the diameter is 1.2 mm, the current is the variable parameter, and the other parameters are a voltage of 20 V, an arc length of 3.2 mm, a wire feed angle of 30°, a wire feed speed of 140 cm/min, a welding speed of 3 mm/sec, and an argon flow amount of 10 L/min. The welding wires manufactured according to each of the examples and comparative examples are used to weld the base material of the 7XXX series high-strength aluminum alloy general-purpose welding wire (7050, 7055, 7075), and then T6 heat treatment is performed or not performed to obtain test samples, which are then tested for mechanical properties according to the room temperature tensile method of GB/T228.1-2010 Metallic Material Tensile Test Part 1, and the room temperature tensile mechanical properties of the welded parts are tested, and two identical samples are arranged for each group of heat-treated samples, and the average value is taken. The test results are shown in Table 4.
実施例３の溶接ワイヤを使用して７０７５母材を溶接した後の溶接継手の外観は、図１で示され、その溶接プロセスと熱処理前後の性能結果は、表３で示される。
The appearance of the welded joint after welding the 7075 base metal using the welding wire of Example 3 is shown in FIG. 1, and the welding process and performance results before and after heat treatment are shown in Table 3.
表３及び図１から分かるように、１６０～１６５Ａの電流で、実施例３の溶接ワイヤを使用して７０７５母材をアルゴンアーク溶接し、優れた溶接性能があり、Ｔ６熱処理前に、２７０ＭＰａ以上の引張強度、５．５％の伸び率があり、Ｔ６熱処理後に、５００ＭＰａ以上の引張強度、１３％の伸び率があり、実施例３の溶接ワイヤは、７０７５母材に対して優れた溶接性能を有することを示す。
As can be seen from Table 3 and FIG. 1 , the welding wire of Example 3 was used to argon arc weld 7075 base metal at a current of 160 to 165 A, and excellent welding performance was obtained. Before the T6 heat treatment, the tensile strength was 270 MPa or more and the elongation rate was 5.5%, and after the T6 heat treatment, the tensile strength was 500 MPa or more and the elongation rate was 13%, which shows that the welding wire of Example 3 has excellent welding performance for 7075 base metal.
表４から分かるように、実施例１における溶接ワイヤ（Ａｌ－７．８Ｚｎ－２．３Ｍｇ－２Ｃｕを母材として０．１％Ｂ＋０．１％Ｚｒを加える）はそれぞれ７０５０母材、７０５５母材、７０７５母材に対して優れた溶接性能を有し、熱処理前後に、７０５０母材を溶接した後の溶接継手の引張強度が８５．７％増加し、伸び率が１２．３６％に増加し、７０５５母材を溶接した後の溶接継手の引張強度が９６．２％増加し、伸び率が１２．８８％に増加し、７０７５母材を溶接した後の溶接継手の引張強度が９２．７％増加し、伸び率が１２．４７％に増加する。 As can be seen from Table 4, the welding wire in Example 1 (Al-7.8Zn-2.3Mg-2Cu as the base material with 0.1%B+0.1%Zr added) has excellent welding performance for 7050 base material, 7055 base material, and 7075 base material, respectively. Before and after heat treatment, the tensile strength of the welded joint after welding the 7050 base material increases by 85.7% and the elongation increases to 12.36%, the tensile strength of the welded joint after welding the 7055 base material increases by 96.2% and the elongation increases to 12.88%, and the tensile strength of the welded joint after welding the 7075 base material increases by 92.7% and the elongation increases to 12.47%.
実施例２における溶接ワイヤ（Ａｌ－７．８Ｚｎ－２．３Ｍｇ－２Ｃｕを母材として０．２％Ｂ＋０．５％Ｚｒを加える）はそれぞれ７０５０母材、７０５５母材、７０７５母材に対して優れた溶接性能を有し、熱処理前後に、７０５０母材を溶接した後の溶接継手の引張強度が１００％以上増加し、伸び率が１１％に増加し、７０５５母材を溶接した後の溶接継手の引張強度が９４．６％増加し、伸び率が１２．４２％に増加し、７０７５母材を溶接した後の溶接継手の引張強度が１００％以上増加し、伸び率が１２．３８％に増加する。 The welding wire in Example 2 (Al-7.8Zn-2.3Mg-2Cu as the base material with 0.2%B+0.5%Zr added) has excellent welding performance for 7050 base material, 7055 base material, and 7075 base material, respectively. Before and after heat treatment, the tensile strength of the welded joint after welding the 7050 base material increases by more than 100% and the elongation increases to 11%, the tensile strength of the welded joint after welding the 7055 base material increases by 94.6% and the elongation increases to 12.42%, and the tensile strength of the welded joint after welding the 7075 base material increases by more than 100% and the elongation increases to 12.38%.
実施例３における溶接ワイヤ（Ａｌ－７．８Ｚｎ－２．３Ｍｇ－２Ｃｕを母材として０．２％Ｂ＋０．３％Ｚｒを加える）はそれぞれ７０５０母材、７０５５母材、７０７５母材に対して優れた溶接性能を有し、熱処理前後に、７０５０母材を溶接した後の溶接継手の引張強度が９２．４％増加し、伸び率が１２．７９％に増加し、７０５５母材を溶接した後の溶接継手の引張強度が１００％以上増加し、伸び率が１２．５６％に増加し、７０７５母材を溶接した後の溶接継手の引張強度が８８．３％増加し、伸び率が１３．７６％に増加する。 The welding wire in Example 3 (Al-7.8Zn-2.3Mg-2Cu as the base material with 0.2% B + 0.3% Zr added) has excellent welding performance for 7050 base material, 7055 base material, and 7075 base material, respectively. Before and after heat treatment, the tensile strength of the welded joint after welding the 7050 base material increases by 92.4% and the elongation increases to 12.79%, the tensile strength of the welded joint after welding the 7055 base material increases by more than 100% and the elongation increases to 12.56%, and the tensile strength of the welded joint after welding the 7075 base material increases by 88.3% and the elongation increases to 13.76%.
実施例４における溶接ワイヤ（Ａｌ－７．８Ｚｎ－２．３Ｍｇ－２Ｃｕを母材として０．４％Ｂ＋０．４％Ｚｒを加える）はそれぞれ７０５０母材、７０５５母材、７０７５母材に対して優れた溶接性能を有し、熱処理前後に、７０５０母材を溶接した後の溶接継手の引張強度が９４．１％増加し、伸び率が１３．２４％に増加し、７０５５母材を溶接した後の溶接継手の引張強度が１００％以上増加し、伸び率が１２．８４％に増加し、７０７５母材を溶接した後の溶接継手の引張強度が９２．０％増加し、伸び率が１３．２４％に増加する。 The welding wire in Example 4 (Al-7.8Zn-2.3Mg-2Cu as the base material with 0.4%B+0.4%Zr added) has excellent welding performance for 7050 base material, 7055 base material, and 7075 base material, respectively. Before and after heat treatment, the tensile strength of the welded joint after welding the 7050 base material increases by 94.1% and the elongation increases to 13.24%, the tensile strength of the welded joint after welding the 7055 base material increases by more than 100% and the elongation increases to 12.84%, and the tensile strength of the welded joint after welding the 7075 base material increases by 92.0% and the elongation increases to 13.24%.
以上のデータから分かるように、本発明では、Ａｌ－７．８Ｚｎ－２．３Ｍｇ－２Ｃｕ系アルミニウム合金に、合計量が１％未満のＢ及びＺｒを加えることによって製造された溶接ワイヤは、７ＸＸＸシリーズの高強度アルミニウム合金に対して優れた溶接性能を有し、溶接後の溶接継手の引張強度及び伸び率はいずれも高くなり、７０５０、７０５５及び７０７５などの７ＸＸＸシリーズの高強度アルミニウム合金、特にＡｌ－Ｚｎ－Ｍｇ－Ｃｕ系高硬度アルミニウム合金の溶接には、汎用性があり、それは、７ＸＸＸシリーズの高強度アルミニウム合金溶接用の高品質の原料を提供でき、広い高強度アルミニウム合金の溶接のプロセスウィンドウを得ることができる。 As can be seen from the above data, in the present invention, the welding wire produced by adding less than 1% total amount of B and Zr to Al-7.8Zn-2.3Mg-2Cu aluminum alloy has excellent welding performance for 7XXX series high-strength aluminum alloys, and the tensile strength and elongation of the welded joint after welding are both high, and it is versatile in welding 7XXX series high-strength aluminum alloys such as 7050, 7055 and 7075, especially Al-Zn-Mg-Cu series high hardness aluminum alloys, which can provide high-quality raw materials for welding 7XXX series high-strength aluminum alloys, and obtain a wide process window for welding high-strength aluminum alloys.
以上の内容は、本発明の好ましい実施例に過ぎず、本発明の保護範囲は、それらに限定されるものではなく、本発明で開示された技術的範囲内で当業者が本発明の技術的解決手段及びその概念に従って行う置換又は変更は、本発明の保護範囲に含まれる。 The above contents are merely preferred embodiments of the present invention, and the scope of protection of the present invention is not limited thereto. Any substitutions or modifications made by a person skilled in the art according to the technical solutions and concepts of the present invention within the technical scope disclosed in the present invention are included in the scope of protection of the present invention.
Claims (6)
Ａｌ－Ｚｎ－Ｍｇ－Ｃｕ系アルミニウム合金とＢ及びＺｒを混合した後に合金を溶融し、次に、射出成形によってビレットを得て、前記ビレットを半固体状態で据え込み加工し、インゴットを形成し、前記インゴットを熱間押出して棒材を得てコイル状にするステップ（１）と、
コイル状の前記棒材を焼戻しし、次に、必要な溶接ワイヤの直径まで連続して複数パスの圧延・伸線加工を行い、サイジング、丸め加工、多結晶ダイによる艶出し、微細研磨、洗浄及び乾燥を順次行い、高強度アルミニウム合金の汎用溶接ワイヤを得るステップ（２）と、
を含み、
前記Ａｌ－Ｚｎ－Ｍｇ－Ｃｕ系アルミニウム合金の成分は、重量百分率で、５～８％のＺｎ、１．５～５％のＭｇ、及び１～３％のＣｕを含み、残部がＡｌであり、
Ｂ及びＺｒの添加量はそれぞれ前記Ａｌ－Ｚｎ－Ｍｇ－Ｃｕ系アルミニウム合金の重量の０．１～１重量％であることを特徴とする、高強度アルミニウム合金の汎用溶接ワイヤの製造方法。 A method for producing a general-purpose welding wire of a high-strength aluminum alloy, comprising the steps of:
(1) mixing an Al-Zn-Mg-Cu based aluminum alloy with B and Zr, melting the alloy, then obtaining a billet by injection molding, upsetting the billet in a semi-solid state to form an ingot, and hot extruding the ingot to obtain a rod and coil it;
(2) tempering the coiled rod, and then subjecting it to multiple passes of rolling and drawing to a required welding wire diameter, followed by sizing, rounding, polishing with a polycrystalline die, fine polishing, cleaning and drying to obtain a high-strength aluminum alloy general-purpose welding wire;
Including,
The composition of the Al-Zn-Mg-Cu based aluminum alloy is, by weight percentage, 5 to 8% Zn, 1.5 to 5% Mg, and 1 to 3% Cu, with the balance being Al;
A method for producing a general-purpose welding wire of a high-strength aluminum alloy, characterized in that the amounts of B and Zr added are each 0.1 to 1 wt % of the weight of the Al-Zn-Mg-Cu-based aluminum alloy.
Ａｌ－Ｚｎ－Ｍｇ－Ｃｕ系アルミニウム合金とＢ及びＺｒを混合した後に合金を溶融し、次に、射出成形によってビレットを得て、前記ビレットを半固体状態で据え込み加工し、インゴットを形成し、前記インゴットを熱間押出して棒材を得てコイル状にするステップ（１）と、
コイル状の前記棒材を焼戻しし、次に、必要な溶接ワイヤの直径まで連続して複数パスの圧延・伸線加工を行い、サイジング、丸め加工、多結晶ダイによる艶出し、微細研磨、洗浄及び乾燥を順次行い、高強度アルミニウム合金の汎用溶接ワイヤを得るステップ（２）と、
を含み、
前記Ａｌ－Ｚｎ－Ｍｇ－Ｃｕ系アルミニウム合金の成分は、重量百分率で、７～８％のＺｎ、２～３％のＭｇ、及び１．５～２．５％のＣｕを含み、残部がＡｌであり、
Ｂ及びＺｒの添加量はそれぞれ前記Ａｌ－Ｚｎ－Ｍｇ－Ｃｕ系アルミニウム合金の重量の０．１～１重量％であることを特徴とする、高強度アルミニウム合金の汎用溶接ワイヤの製造方法。 A method for producing a general-purpose welding wire of a high-strength aluminum alloy, comprising the steps of:
(1) mixing an Al-Zn-Mg-Cu based aluminum alloy with B and Zr, melting the alloy, then obtaining a billet by injection molding, upsetting the billet in a semi-solid state to form an ingot, and hot extruding the ingot to obtain a rod and coil it;
(2) tempering the coiled rod, and then subjecting it to multiple passes of rolling and drawing to a required welding wire diameter, followed by sizing, rounding, polishing with a polycrystalline die, fine polishing, cleaning and drying to obtain a high-strength aluminum alloy general-purpose welding wire;
Including,
The composition of the Al-Zn-Mg-Cu based aluminum alloy is, by weight percentage, 7 to 8% Zn, 2 to 3% Mg, and 1.5 to 2.5% Cu, with the balance being Al;
A method for producing a general-purpose welding wire of a high-strength aluminum alloy, characterized in that the amounts of B and Zr added are each 0.1 to 1 wt % of the weight of the Al-Zn-Mg-Cu-based aluminum alloy.
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| US20100276108A1 (en) | 2009-04-29 | 2010-11-04 | Israel Stol | 7xxx weld filler alloys and methods of using the same |
| CN112593129A (en) | 2020-12-11 | 2021-04-02 | 江苏科技大学 | ZrB2Ceramic particle modified Al-Zn-Mg-Cu aluminum alloy welding rod and preparation method thereof |
| CN112831735A (en) | 2020-12-30 | 2021-05-25 | 江苏理工学院 | A kind of preparation method of high-strength aluminum alloy wire/strip |
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