JP5757104B2 - Magnesium alloy material and manufacturing method thereof - Google Patents

Magnesium alloy material and manufacturing method thereof Download PDF

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JP5757104B2
JP5757104B2 JP2011038888A JP2011038888A JP5757104B2 JP 5757104 B2 JP5757104 B2 JP 5757104B2 JP 2011038888 A JP2011038888 A JP 2011038888A JP 2011038888 A JP2011038888 A JP 2011038888A JP 5757104 B2 JP5757104 B2 JP 5757104B2
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magnesium alloy
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plate
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JP2012172254A (en
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大石 幸広
幸広 大石
森 信之
信之 森
龍一 井上
龍一 井上
河部 望
望 河部
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Sumitomo Electric Industries Ltd
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    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C23/00Alloys based on magnesium
    • C22C23/02Alloys based on magnesium with aluminium as the next major constituent
    • BPERFORMING OPERATIONS; TRANSPORTING
    • B21MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21BROLLING OF METAL
    • B21B3/00Rolling materials of special alloys so far as the composition of the alloy requires or permits special rolling methods or sequences Rolling of aluminium, copper, zinc or other non-ferrous metals
    • BPERFORMING OPERATIONS; TRANSPORTING
    • B22CASTING; POWDER METALLURGY
    • B22DCASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D11/00Continuous casting of metals, i.e. casting in indefinite lengths
    • B22D11/001Continuous casting of metals, i.e. casting in indefinite lengths of specific alloys
    • BPERFORMING OPERATIONS; TRANSPORTING
    • B22CASTING; POWDER METALLURGY
    • B22DCASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D11/00Continuous casting of metals, i.e. casting in indefinite lengths
    • B22D11/06Continuous casting of metals, i.e. casting in indefinite lengths into moulds with travelling walls, e.g. with rolls, plates, belts, caterpillars
    • BPERFORMING OPERATIONS; TRANSPORTING
    • B22CASTING; POWDER METALLURGY
    • B22DCASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D11/00Continuous casting of metals, i.e. casting in indefinite lengths
    • B22D11/06Continuous casting of metals, i.e. casting in indefinite lengths into moulds with travelling walls, e.g. with rolls, plates, belts, caterpillars
    • B22D11/0622Continuous casting of metals, i.e. casting in indefinite lengths into moulds with travelling walls, e.g. with rolls, plates, belts, caterpillars formed by two casting wheels
    • BPERFORMING OPERATIONS; TRANSPORTING
    • B22CASTING; POWDER METALLURGY
    • B22DCASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D21/00Casting non-ferrous metals or metallic compounds so far as their metallurgical properties are of importance for the casting procedure; Selection of compositions therefor
    • B22D21/02Casting exceedingly oxidisable non-ferrous metals, e.g. in inert atmosphere
    • B22D21/04Casting aluminium or magnesium
    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C1/00Making alloys
    • C22C1/02Making alloys by melting
    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C23/00Alloys based on magnesium
    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22FCHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/06Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of magnesium or alloys based thereon
    • CCHEMISTRY; METALLURGY
    • C21METALLURGY OF IRON
    • C21DMODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2201/00Treatment for obtaining particular effects
    • C21D2201/05Grain orientation
    • YGENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10TECHNICAL SUBJECTS COVERED BY FORMER USPC
    • Y10TTECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
    • Y10T428/00Stock material or miscellaneous articles
    • Y10T428/12All metal or with adjacent metals

Description

本発明は、自動車や鉄道車両、飛行機などの輸送機器の部品や自転車部品、電子・電気機器の筐体、その他の構造部材といった各種の部材、及び当該部材の構成材料に適したマグネシウム合金材、並びにその製造方法に関するものである。特に、肉厚で、プレス加工といった塑性加工性に優れるマグネシウム合金材に関するものである。   The present invention relates to various members such as parts of transportation equipment such as automobiles, railway vehicles, airplanes, bicycle parts, casings of electronic / electric equipment, and other structural members, and magnesium alloy materials suitable for constituent materials of the members, And a manufacturing method thereof. In particular, the present invention relates to a magnesium alloy material that is thick and excellent in plastic workability such as press working.

携帯電話やノート型パーソナルコンピュータといった携帯用電子・電気機器類の筐体、ホィールカバーやパドルシフトなどの自動車部品、鉄道車両部品、フレームなどの自転車部品といった各種の部材の構成材料として、軽量で、比強度、比剛性に優れるマグネシウム合金が検討されている。マグネシウム合金からなる部材は、ダイカスト法やチクソモールド法による鋳造材(ASTM規格のAZ91合金)が主流である。近年、ASTM規格のAZ31合金に代表される展伸用マグネシウム合金からなる板にプレス加工を施したプレス加工材が使用されつつある。特許文献1では、双ロール鋳造法を用いて、AZ91合金などの各種のマグネシウム合金からなる連続鋳造材を作製し、この連続鋳造材に圧延を施して得られた圧延板にプレス加工を施すことを開示している。   It is lightweight as a component material for various components such as casings for portable electronic and electrical equipment such as mobile phones and notebook personal computers, automobile parts such as wheel covers and paddle shifts, railway vehicle parts, and bicycle parts such as frames. Magnesium alloys excellent in specific strength and specific rigidity have been studied. As for the members made of magnesium alloy, casting materials (ASTM standard AZ91 alloy) by die casting method or thixo mold method are mainly used. In recent years, a press-worked material obtained by press-working a plate made of a magnesium alloy for extension represented by ASTM standard AZ31 alloy is being used. In Patent Document 1, a continuous cast material made of various magnesium alloys such as AZ91 alloy is produced using a twin roll casting method, and a rolled plate obtained by rolling the continuous cast material is subjected to press working. Is disclosed.

国際公開第2006/003899号International Publication No. 2006/003899

従来、マグネシウム合金の軽量性に着目して、プレス加工材といった塑性加工材の素材には、厚さ1mm以下といった比較的薄い板材が検討されている。しかし、マグネシウム合金の用途範囲の拡大に伴い、上述のような薄板だけでなく、比強度、比剛性に着目して肉厚なもの、具体的には、厚さ1.5mm以上の厚い板材の開発が望まれる。従来、このような肉厚で塑性加工性に優れるマグネシウム合金板といった素材、及びその製造方法、並びにこの板を用いて作製したプレス加工材といった塑性加工材について十分に検討されていない。   Conventionally, a relatively thin plate material having a thickness of 1 mm or less has been studied as a material of a plastic work material such as a press work material, focusing on the light weight of a magnesium alloy. However, with the expansion of the range of applications of magnesium alloys, not only the above-mentioned thin plates, but also the development of thick plates with a focus on specific strength and specific rigidity, specifically thick plates with a thickness of 1.5 mm or more Is desired. Conventionally, a material such as a magnesium alloy plate having such a thickness and excellent plastic workability, a manufacturing method thereof, and a plastic work material such as a press work material produced using this plate have not been sufficiently studied.

ダイカスト法やチクソモールド法を利用すれば、肉厚なマグネシウム合金板が得られる。しかし、ダイカスト材といった鋳造材では、巣といった内部欠陥が存在し易い上に、添加元素成分が局所的に高濃度になったり、結晶粒がランダムに配向したりするなど、組成や組織が不均一になり易い。また、ダイカスト材といった鋳造材では、析出物が結晶粒界に析出し易い。上記欠陥部分や結晶粒界の析出物などが破壊の起点となることで、ダイカスト材といった鋳造材は、プレス加工などの塑性加工性に劣る。また、ダイカスト材といった鋳造材は、上記内部欠陥などにより、プレス加工材といった塑性加工材よりも強度や硬度などの機械的特性に劣る。   If a die casting method or a thixo mold method is used, a thick magnesium alloy plate can be obtained. However, in casting materials such as die-cast materials, internal defects such as nests are likely to exist, and the composition and structure are not uniform, such as locally high concentrations of additive element components and random orientation of crystal grains. It is easy to become. Further, in a cast material such as a die-cast material, precipitates are likely to precipitate at the grain boundaries. Casting materials such as die-cast materials are inferior in plastic workability such as press work, because the defect portion and the precipitates at the crystal grain boundaries are the starting points of fracture. Further, a cast material such as a die-cast material is inferior in mechanical properties such as strength and hardness to a plastic material such as a press-worked material due to the above internal defects.

そこで、本発明の目的の一つは、肉厚で塑性加工性に優れるマグネシウム合金材や塑性加工が施された肉厚なマグネシウム合金材を提供することにある。また、本発明の他の目的は、肉厚で塑性加工性に優れるマグネシウム合金材が得られるマグネシウム合金材の製造方法を提供することにある。   Accordingly, one of the objects of the present invention is to provide a magnesium alloy material that is thick and excellent in plastic workability, and a thick magnesium alloy material that has been subjected to plastic working. Another object of the present invention is to provide a method for producing a magnesium alloy material from which a magnesium alloy material having a large thickness and excellent plastic workability can be obtained.

ダイカスト材やチクソモールド材に比較して、圧延などの塑性加工(1次加工)が施されたマグネシウム合金材は、鋳造時の欠陥が低減されたり、結晶が微細化されたりすることで、同一の組成であっても、強度や硬度、靭性などの機械的特性、耐食性、塑性加工性に優れる。また、上記1次加工を施したマグネシウム合金材にプレス加工などの塑性加工(2次加工)を施したマグネシウム合金材も、上記機械的特性や耐食性に優れる。特に、1次加工材の素材として双ロール鋳造法といった連続鋳造法により製造した連続鋳造材を利用すると、当該鋳造材は、偏析や粗大な晶析出物がダイカスト材などに比較して少なく、塑性加工性に優れる。そこで、本発明者らは、連続鋳造材に種々の条件で圧延を施して、厚さ1.5mm以上の肉厚なマグネシウム合金板を作製して、その塑性加工性を調べた。ここで、マグネシウム合金の圧延材(圧延板)は、一般に、マグネシウム合金の結晶の底面が圧延方向(圧延される素材が進行する方向)に平行に配向した集合組織を有する。しかし、上記集合組織における集積度が強いと、プレス加工などの塑性加工時、成形性を損なうという欠点を有する。本発明者らは、(1)圧延板の表面側部分における集合組織が圧延板の内部部分における集合組織と比較して集積度が強い場合、成形性(塑性加工性)の低下が大きい、(2)肉厚な素材に従来の圧延を施して肉厚な圧延材を得ようとすると、その表面側部分における集合組織が内部部分に比較して発達して、厚さが1.5mm以下といった薄板と同程度の成形性が得られない、との知見を得た。更に、本発明者らは、特定の条件で作製したマグネシウム合金板は、肉厚でありながら、プレス加工といった塑性加工性に優れる、との知見を得た。本発明は、上記知見に基づくものである。   Compared to die-casting materials and thixo-mold materials, magnesium alloy materials that have been subjected to plastic processing (primary processing) such as rolling are the same by reducing defects during casting and making crystals finer. Even with this composition, mechanical properties such as strength, hardness and toughness, corrosion resistance, and plastic workability are excellent. A magnesium alloy material obtained by subjecting the magnesium alloy material subjected to the primary processing to plastic processing (secondary processing) such as press working is also excellent in the mechanical characteristics and corrosion resistance. In particular, when a continuous cast material manufactured by a continuous casting method such as a twin roll casting method is used as a material for the primary work material, the cast material has less segregation and coarse crystal precipitates than plastics such as die casting, and is plastic. Excellent workability. Therefore, the present inventors rolled the continuous cast material under various conditions to produce a thick magnesium alloy plate having a thickness of 1.5 mm or more, and investigated its plastic workability. Here, the rolled material (rolled plate) of the magnesium alloy generally has a texture in which the bottom surface of the magnesium alloy crystal is oriented parallel to the rolling direction (the direction in which the rolled material proceeds). However, if the degree of integration in the texture is strong, there is a disadvantage that the formability is impaired during plastic processing such as press processing. The inventors of the present invention (1) when the texture in the surface side portion of the rolled plate is stronger than the texture in the inner portion of the rolled plate, the decrease in formability (plastic workability) is large. 2) When trying to obtain a thick rolled material by subjecting a thick material to conventional rolling, the texture on the surface side part develops compared to the internal part, and the thickness is 1.5 mm or less. As a result, it was found that the same moldability as that of the material was not obtained. Furthermore, the present inventors have obtained the knowledge that a magnesium alloy plate produced under specific conditions is excellent in plastic workability such as press working while being thick. The present invention is based on the above findings.

本発明のマグネシウム合金材は、マグネシウム合金からなり、厚さが1.5mm以上の板状部を有し、かつ、この板状部が以下の配向性を満たす。
[配向性]
上記板状部の表面から厚さ方向に厚さの1/4までの領域を表面領域、残部の領域を内部領域とし、
上記表面領域における(002)面、(100)面、(101)面、(102)面、(110)面、及び(103)面のX線回折のピーク強度をそれぞれIF(002)、IF(100)、IF(101)、IF(102)、IF(110)、及びIF(103)とし、
上記内部領域における(002)面、(100)面、(101)面、(102)面、(110)面、及び(103)面のX線回折のピーク強度をそれぞれIC(002)、IC(100)、IC(101)、IC(102)、IC(110)、及びIC(103)とし、
上記表面領域における(002)面の配向度合い:IF(002)/{IF(100)+IF(002)+IF(101)+IF(102)+IF(110)+IF(103)}を底面ピーク比OF
上記内部領域における(002)面の配向度合い:IC(002)/{IC(100)+IC(002)+IC(101)+IC(102)+IC(110)+IC(103)}を底面ピーク比OCとするとき、
上記内部領域の底面ピーク比Ocに対する上記表面領域の底面ピーク比OFの比率:OF/Ocが、0.95≦OF/Oc≦1.05を満たす。
The magnesium alloy material of the present invention is made of a magnesium alloy, has a plate-like portion having a thickness of 1.5 mm or more, and the plate-like portion satisfies the following orientation.
[Orientation]
The area from the surface of the plate-shaped part to 1/4 of the thickness in the thickness direction is the surface area, the remaining area is the internal area,
The X-ray diffraction peak intensities of the (002) plane, (100) plane, (101) plane, (102) plane, (110) plane, and (103) plane in the surface region are respectively I F (002), I F (100), I F (101), I F (102), I F (110), and I F (103),
The peak intensities of X-ray diffraction of the (002) plane, (100) plane, (101) plane, (102) plane, (110) plane, and (103) plane in the internal region are I C (002), I C (100), I C (101), I C (102), I C (110), and I C (103)
Orientation degree of (002) plane in the surface region: I F (002) / { I F (100) + I F (002) + I F (101) + I F (102) + I F (110) + I F (103)} a bottom peak ratio O F,
Orientation degree of (002) plane in the internal region: I C (002) / {I C (100) + I C (002) + I C (101) + I C (102) + I C (110) + I C (103)} when the the bottom peak ratio O C,
The ratio of the bottom peak ratio O F of the surface area relative to the bottom surface peak ratio O c of the internal region: O F / O c satisfies the 0.95 ≦ O F / O c ≦ 1.05.

上記本発明マグネシウム合金材は、例えば、以下の本発明製造方法により製造することができる。本発明のマグネシウム合金材の製造方法は、マグネシウム合金からなる素材に圧延を施してマグネシウム合金材を製造する方法に係るものであり、以下の準備工程と、圧延工程とを具える。
準備工程:溶解したマグネシウム合金を双ロール鋳造法により連続鋳造した板状の素材を準備する工程。
圧延工程:上記素材に複数パスの圧延を施して、厚さ1.5mm以上の板状のマグネシウム合金材を製造する工程。
この圧延工程では、1パスあたりの圧下率が25%以上の圧延を少なくとも1パス行い、残りの各パスの圧下率を10%以上とする。
なお、圧下率(%)とは、{(圧延前の素材の厚さtb−圧延後の素材の厚さta)/圧延前の素材の厚さtb}×100をいう。
The said magnesium alloy material of this invention can be manufactured with the following this invention manufacturing method, for example. The method for producing a magnesium alloy material according to the present invention relates to a method for producing a magnesium alloy material by rolling a material made of a magnesium alloy, and includes the following preparation step and rolling step.
Preparation step: A step of preparing a plate-like material obtained by continuously casting a molten magnesium alloy by a twin roll casting method.
Rolling step: A step of producing a plate-like magnesium alloy material having a thickness of 1.5 mm or more by subjecting the material to rolling in a plurality of passes.
In this rolling process, at least one pass of rolling with a reduction rate of 25% or more per pass is performed, and the reduction rate of each remaining pass is set to 10% or more.
The reduction ratio (%) means {(thickness t b of material before rolling−thickness t a of material after rolling) / thickness t b of material before rolling} × 100.

上記本発明製造方法によれば、割れなどの起点となる欠陥や晶析出物、偏析が少ない、或いは実質的に存在しない連続鋳造材を素材とすることで、1パスあたりの圧下率が25%以上という比較的強加工な圧延を良好に施すことができる。また、この圧下率が高い圧延では、素材の厚さ方向の全域に亘って、均一的に塑性加工を施すことができる。即ち、圧下率が高い圧延を少なくとも1パス行うことで、素材の表面から内部に亘って、均一的に加工することができる。従って、本発明製造方法によれば、厚さ方向の全域に亘って均一的な組織により構成されたマグネシウム合金材(代表的には圧延板(本発明マグネシウム合金材の一形態))が得られる。この組織は、マグネシウム合金の結晶の底面が圧延方向に平行するように主に配列した集合組織(上記結晶のc軸が圧延方向に直交するように配列した集合組織)である。   According to the production method of the present invention, the reduction rate per pass is 25% by using a continuous casting material that has few or substantially no defects, crystal precipitates, segregation, or the like as a starting point such as cracks. The relatively strong rolling as described above can be performed satisfactorily. Moreover, in this rolling with a high rolling reduction, plastic working can be performed uniformly over the entire region in the thickness direction of the material. That is, by performing at least one pass of rolling with a high rolling reduction, uniform processing can be performed from the surface of the material to the inside. Therefore, according to the manufacturing method of the present invention, a magnesium alloy material (typically a rolled plate (one form of the magnesium alloy material of the present invention)) having a uniform structure over the entire region in the thickness direction can be obtained. . This structure is a texture that is arranged mainly so that the bottom surface of the magnesium alloy crystal is parallel to the rolling direction (a texture that is arranged so that the c-axis of the crystal is perpendicular to the rolling direction).

本発明マグネシウム合金材が上述の特定の圧延が施された圧延板である場合(即ち、本発明マグネシウム合金材の全体が板状部から構成される形態の場合)、上述のようにその厚さ方向の全域(表面〜中央〜表面)に亘って均一的な組織により構成される。このような均一的な組織から構成されることでこの本発明マグネシウム合金材は、肉厚でありながら、プレス加工といった塑性加工性に優れる。従って、この板状のマグネシウム合金材は、プレス加工といった塑性加工用素材に好適に利用できる。また、このマグネシウム合金材は、均一的な組織から構成されることで、均一的な特性(硬度や強度、耐衝撃性、靭性などの機械的特性、耐食性、制振性など)も有する。更に、上記板状のマグネシウム合金材を塑性加工用素材に利用した場合、寸法精度に優れるプレス加工材といった塑性加工材(本発明マグネシウム合金材の一形態)が得られる。得られた塑性加工材もその厚さ方向の全域に亘って均一的な組織から構成される、即ち、上記素材の組織を実質的に維持する。従って、得られたプレス加工材といった塑性加工材も上記均一的な特性を有する。   When the magnesium alloy material of the present invention is a rolled plate subjected to the above-described specific rolling (that is, when the entire magnesium alloy material of the present invention is composed of a plate-shaped portion), the thickness thereof as described above. It is composed of a uniform structure over the entire direction (surface to center to surface). By being composed of such a uniform structure, the magnesium alloy material of the present invention is excellent in plastic workability such as press working while being thick. Therefore, this plate-like magnesium alloy material can be suitably used as a material for plastic working such as press working. In addition, this magnesium alloy material is composed of a uniform structure, and thus has uniform characteristics (mechanical characteristics such as hardness, strength, impact resistance, toughness, corrosion resistance, vibration damping, etc.). Further, when the plate-like magnesium alloy material is used as a material for plastic working, a plastic working material (one form of the magnesium alloy material of the present invention) such as a press working material having excellent dimensional accuracy can be obtained. The obtained plastic working material is also composed of a uniform structure over the entire region in the thickness direction, that is, substantially maintains the structure of the material. Therefore, the obtained plastic working material such as press working material also has the above-mentioned uniform characteristics.

本発明マグネシウム合金材の一形態として、上記表面領域の平均結晶粒径をDF、上記内部領域の平均結晶粒径をDcとするとき、上記表面領域の平均結晶粒径DFに対する上記内部領域の平均結晶粒径Dcの比率:Dc/DFが、2/3≦Dc/DF≦3/2を満たし、かつ、DF及びDc≧3.5μmである形態が挙げられる。 As an embodiment of the magnesium alloy material of the present invention, when the average crystal grain size of the surface region is D F and the average crystal grain size of the internal region is D c , the internal region with respect to the average crystal grain size D F of the surface region is The ratio of the average crystal grain diameter D c in the region: D c / D F satisfies 2/3 ≦ D c / D F ≦ 3/2, and D F and D c ≧ 3.5 μm .

上記形態によれば、厚さ方向の全域に亘って均一的な粒径であるため、塑性加工性により優れる。   According to the said form, since it is a uniform particle diameter over the whole area of the thickness direction, it is excellent by plastic workability.

本発明マグネシウム合金材の一形態として、上記表面領域のビッカース硬度(Hv)をHF、上記内部領域のビッカース硬度(Hv)をHcとするとき、上記表面領域のビッカース硬度HFに対する上記内部領域のビッカース硬度Hcの比率:Hc/HFが、0.85≦Hc/HF≦1.2を満たす形態が挙げられる。 As one embodiment of the magnesium alloy material of the present invention, when the Vickers hardness (Hv) of the surface region is H F and the Vickers hardness (Hv) of the internal region is H c , the internal to the Vickers hardness H F of the surface region the ratio of the Vickers hardness H c region: H c / H F may include forms that satisfies 0.85 ≦ H c / H F ≦ 1.2.

上記形態によれば、厚さ方向の全域に亘って均一的な硬度を有するため、例えば、当該マグネシウム合金材の一部に、研削加工や化学的処理などを施して、部分的に表面側部分を除去した場合でも、当該加工や処理後のマグネシウム合金材は、その表面硬度が当該加工や処理の前と実質的に変化せず、安定した表面性状を有する。従って、上記形態によれば、後工程で化成処理などの表面処理を行う場合に、当該処理を安定して行える。   According to the above aspect, since it has a uniform hardness over the entire region in the thickness direction, for example, a part of the magnesium alloy material is subjected to grinding or chemical treatment, and the surface side portion is partially applied. Even when is removed, the surface hardness of the magnesium alloy material after the processing or treatment does not substantially change from that before the processing or treatment, and has stable surface properties. Therefore, according to the said form, when performing surface treatments, such as a chemical conversion treatment, in the post process, the said process can be performed stably.

本発明マグネシウム合金材は、種々の元素を添加元素とするマグネシウム合金(残部Mg及び不純物)から構成され得る。特に、添加元素の濃度が高い合金、具体的には合計含有量が5.0質量%以上であるマグネシウム合金は、添加元素の種類にもよるが、強度や硬度といった機械的特性、耐食性、難燃性、耐熱性といった種々の特性に優れる。   The magnesium alloy material of the present invention can be composed of magnesium alloys (remainder Mg and impurities) containing various elements as additive elements. In particular, alloys with high concentrations of additive elements, specifically magnesium alloys with a total content of 5.0% by mass or more, depend on the type of additive elements, but mechanical properties such as strength and hardness, corrosion resistance, and flame resistance Excellent in various properties such as heat resistance.

具体的な添加元素は、Al,Zn,Mn,Si,Be,Ca,Sr,Y,Cu,Ag,Sn,Li,Zr,Ce,Ni,Au及び希土類元素(Y,Ceを除く)から選択される少なくとも1種の元素が挙げられる。不純物は、例えば、Feなどが挙げられる。   Specific additive elements are selected from Al, Zn, Mn, Si, Be, Ca, Sr, Y, Cu, Ag, Sn, Li, Zr, Ce, Ni, Au, and rare earth elements (excluding Y and Ce) And at least one element. Examples of the impurity include Fe.

特に、Alを含有するMg-Al系合金は、耐食性に優れる上に、強度や硬度といった機械的特性にも優れる。従って、本発明マグネシウム合金材の一形態として、上記マグネシウム合金が添加元素にAlを5.0質量%以上12質量%以下含有する形態が挙げられる。Alの含有量が多いほど上記効果が高い傾向にあり、7質量%以上、更に7.3質量%以上が好ましい。但し、Alの含有量が12質量%を超えると塑性加工性の低下を招くことから、上限は12質量%、更に11質量%が好ましい。特に、Alを8.3質量%〜9.5質量%含有する形態は、強度及び耐食性により優れる。Al以外の各元素の含有量は、合計で0.01質量%以上10質量%以下、好ましくは0.1質量%以上5質量%以下が挙げられる。   In particular, Mg-Al alloys containing Al are excellent in corrosion resistance and mechanical properties such as strength and hardness. Therefore, as an embodiment of the magnesium alloy material of the present invention, an embodiment in which the magnesium alloy contains 5.0% by mass or more and 12% by mass or less of Al as an additive element. The higher the Al content, the higher the above effect tends to be, and 7 mass% or more, and preferably 7.3 mass% or more are preferable. However, if the Al content exceeds 12% by mass, the plastic workability is lowered, so the upper limit is preferably 12% by mass, and more preferably 11% by mass. In particular, the form containing 8.3 mass% to 9.5 mass% of Al is more excellent in strength and corrosion resistance. The total content of each element other than Al is 0.01% by mass or more and 10% by mass or less, preferably 0.1% by mass or more and 5% by mass or less.

Mg-Al系合金のより具体的な組成は、例えば、ASTM規格におけるAZ系合金(Mg-Al-Zn系合金、Zn:0.2質量%〜1.5質量%、例えば、AZ31合金、AZ61合金、AZ91合金など)、AM系合金(Mg-Al-Mn系合金、Mn:0.15質量%〜0.5質量%)、AS系合金(Mg-Al-Si系合金、Si:0.01質量%〜20質量%)、Mg-Al-RE(希土類元素)系合金、AX系合金(Mg-Al-Ca系合金、Ca:0.2質量%〜6.0質量%)、AJ系合金(Mg-Al-Sr系合金、Sr:0.2質量%〜7.0質量%)などが挙げられる。Alを8.3質量%〜9.5質量%含有する合金として、更にZnを0.5質量%〜1.5質量%含有するMg-Al-Zn系合金、代表的にはAZ91合金が挙げられる。   More specific compositions of Mg-Al alloys include, for example, AZ-based alloys according to ASTM standards (Mg-Al-Zn-based alloys, Zn: 0.2 mass% to 1.5 mass%, such as AZ31 alloy, AZ61 alloy, AZ91 alloy) Etc.), AM alloy (Mg-Al-Mn alloy, Mn: 0.15 mass% to 0.5 mass%), AS alloy (Mg-Al-Si alloy, Si: 0.01 mass% to 20 mass%), Mg -Al-RE (rare earth element) alloy, AX alloy (Mg-Al-Ca alloy, Ca: 0.2 mass% to 6.0 mass%), AJ alloy (Mg-Al-Sr alloy, Sr: 0.2 mass) % To 7.0% by mass). Examples of the alloy containing 8.3 mass% to 9.5 mass% of Al further include an Mg—Al—Zn alloy containing 0.5 mass% to 1.5 mass% of Zn, typically AZ91 alloy.

その他、Y,Ce,Ca,Si,Sn及び希土類元素(Y,Ceを除く)から選択される少なくとも1種の元素を合計0.001質量%以上、好ましくは合計0.1質量%以上5質量%以下含有し、残部がMg及び不純物からなるマグネシウム合金は、耐熱性、難燃性に優れる。希土類元素を含有する場合、その合計含有量は0.1質量%以上が好ましく、特に、Yを含有する場合、その含有量は0.5質量%以上が好ましい。   In addition, it contains at least one element selected from Y, Ce, Ca, Si, Sn and rare earth elements (excluding Y and Ce) in a total amount of 0.001% by mass or more, preferably a total of 0.1% by mass or more and 5% by mass or less. The magnesium alloy with the balance being Mg and impurities is excellent in heat resistance and flame retardancy. When the rare earth element is contained, the total content is preferably 0.1% by mass or more, and particularly when Y is contained, the content is preferably 0.5% by mass or more.

本発明マグネシウム合金材は、肉厚で、塑性加工性に優れる。本発明マグネシウム合金材の製造方法は、肉厚で、塑性加工性に優れるマグネシウム合金材を製造することができる。   The magnesium alloy material of the present invention is thick and excellent in plastic workability. The manufacturing method of the magnesium alloy material of the present invention can manufacture a magnesium alloy material that is thick and excellent in plastic workability.

以下、本発明をより詳細に説明する。
[マグネシウム合金材]
(組成)
本発明マグネシウム合金材は、50質量%以上のMgと、代表的には上述した添加元素とを含有するマグネシウム合金により構成される。
The present invention will be described in detail below.
[Magnesium alloy material]
(composition)
The magnesium alloy material of the present invention is composed of a magnesium alloy containing 50% by mass or more of Mg and typically the additive elements described above.

(形態)
本発明マグネシウム合金材に具える板状部とは、平行する一対の面を具え、両面の間隔(両面の間の距離)が実質的に均一である、即ち、厚さが均一である部分を言う。本発明マグネシウム合金材は、その一部に板状部を有していれば、その他部に、ボスなどが接合された形態、溝を有する形態、表裏に貫通する孔を有する形態など、切削加工などの加工により、局所的に厚さが異なる部分を有する形態を許容する。
(Form)
The plate-like portion provided in the magnesium alloy material of the present invention has a pair of parallel surfaces, and the interval between both surfaces (distance between both surfaces) is substantially uniform, that is, a portion where the thickness is uniform. say. If the magnesium alloy material of the present invention has a plate-like part in a part thereof, the cutting process such as a form in which a boss is joined to the other part, a form having a groove, a form having a hole penetrating the front and back, etc. The form which has the part from which thickness differs locally by processing, such as is permitted.

上記板状部を有する本発明マグネシウム合金材の代表的な形態は、その全体が板状である形態(マグネシウム合金板)が挙げられる。このマグネシウム合金板の形状(平面形状)は、矩形、円形状など種々の形状をとり得る。また、このマグネシウム合金板は、連続する長尺材を巻き取ったコイル材、所定の長さ・形状の短尺材のいずれの形態もとり得る。このマグネシウム合金板は、製造工程によっても種々の形態をとり得る。代表的には、圧延板、圧延板に後述する熱処理や矯正を施した熱処理板や矯正板、上記圧延板や熱処理板、矯正板に研磨や塗装を施した研磨板、塗装板などが挙げられる。   A typical form of the magnesium alloy material of the present invention having the plate-like portion includes a form (magnesium alloy plate) whose whole is plate-like. The shape (planar shape) of the magnesium alloy plate can take various shapes such as a rectangle and a circle. Moreover, this magnesium alloy plate can take any form of the coil material which wound up the continuous long material, and the short material of predetermined length and shape. This magnesium alloy plate can take various forms depending on the manufacturing process. Typically, a rolled plate, a heat-treated plate or a straightened plate subjected to heat treatment or correction described later, a rolled plate, a heat-treated plate, a polished plate obtained by polishing or coating the straightened plate, a coated plate, or the like can be given. .

その他、本発明マグネシウム合金材は、上記マグネシウム合金板に、曲げ加工や絞り加工といったプレス加工などの塑性加工(2次加工)を施した成形体、上記塑性加工が一部に施されて、塑性加工部を有する部分加工材が挙げられる(但し、少なくとも一部に上記板状部を有する)。上記成形体は、例えば、天板部(底面部)と、天板部の周縁から立設される側壁部とを有する断面]状の箱体や]状の枠体、天板部が円板状で、側壁部が円筒状の有蓋筒状体などが挙げられる。上記天板部が板状部に相当する。所望の用途に応じて、マグネシウム合金材の形態を選択することができる。   In addition, the magnesium alloy material of the present invention is a molded body obtained by subjecting the magnesium alloy sheet to plastic processing (secondary processing) such as press working such as bending or drawing, and the plastic working is partially applied to the plastic. Examples include a partially processed material having a processed part (however, at least a part of the plate-shaped part is included). The molded body is, for example, a cross-sectional box having a top plate portion (bottom surface portion) and a side wall portion erected from the periphery of the top plate portion, a frame-like frame body, and the top plate portion being a disc. For example, a covered cylindrical body having a cylindrical side wall portion may be used. The top plate portion corresponds to a plate-like portion. Depending on the desired application, the form of the magnesium alloy material can be selected.

(厚さ)
本発明マグネシウム合金材は、上記板状部の厚さが1.5mm以上であることを特徴の一つとする。この厚さは、所望の用途などに応じて、1.5mm以上の任意の値を選択することができる。但し、上記板状部を厚くするには、素材となる鋳造材も厚くする必要がある。鋳造材を厚くすると、上述のように欠陥などで圧延性の低下を招く。従って、上記厚さは10mm以下、特に5mm以下であると、肉厚の圧延板(本発明マグネシウム合金材の一形態)を生産性よく製造できて好ましい。
(thickness)
One feature of the magnesium alloy material of the present invention is that the plate-like portion has a thickness of 1.5 mm or more. As the thickness, an arbitrary value of 1.5 mm or more can be selected according to a desired application. However, in order to increase the thickness of the plate-shaped portion, it is necessary to increase the thickness of the casting material. When the cast material is thickened, the rolling property is deteriorated due to defects as described above. Therefore, it is preferable that the thickness is 10 mm or less, particularly 5 mm or less because a thick rolled plate (one form of the magnesium alloy material of the present invention) can be produced with high productivity.

本発明マグネシウム合金材が上記成形体や上記部分加工材である場合、塑性加工に伴う変形が少ない箇所(代表的には板状部)は、塑性加工の素材となった上記マグネシウム合金板の組織や機械的特性を概ね維持する。   In the case where the magnesium alloy material of the present invention is the molded body or the partially processed material, the portion where the deformation due to plastic processing is small (typically, the plate-like portion) is the structure of the magnesium alloy plate that is the material of the plastic processing. And generally maintain mechanical properties.

(組織)
<配向性>
本発明マグネシウム合金材は、少なくとも上記板状部がその厚さ方向の全域に亘って均一的な集合組織を有する組織から構成されることを特徴の一つとする。上述した底面ピーク比の比率OF/Ocが特に1.00≦OF/Oc≦1.05を満たす形態は、塑性加工性により優れる。また、得られた塑性加工材(成形体)や部分加工材はその全体に亘って機械的特性のばらつきが小さい。
(Organization)
<Orientation>
One feature of the magnesium alloy material of the present invention is that at least the plate-like portion is composed of a structure having a uniform texture throughout the entire thickness direction. A form in which the ratio of the bottom peak ratio O F / O c described above satisfies 1.00 ≦ O F / O c ≦ 1.05 is particularly excellent in plastic workability. In addition, the obtained plastic working material (molded body) and the partially processed material have small variations in mechanical characteristics throughout the whole.

<平均結晶粒径>
本発明マグネシウム合金材の代表的な形態として、上述のように厚さ方向の全域に亘って、結晶粒径が均一的な大きさである形態が挙げられる。この形態は、プレス加工などの塑性加工を施した際、均一的に変形でき、寸法精度に優れる塑性加工材(成形体)や部分加工材が得られる。表面領域と内部領域とにおいて平均結晶粒径の差が小さいほど塑性加工を均一的に行えると期待されるため、上述した平均結晶粒径の比率:Dc/DFが特に1≦Dc/DF≦1.4を満たす形態は、塑性加工性により優れる。また、得られた塑性加工材(成形体)や部分加工材はその全体に亘って機械的特性のばらつきが小さい。
<Average crystal grain size>
A typical form of the magnesium alloy material of the present invention includes a form in which the crystal grain size is uniform over the entire region in the thickness direction as described above. In this form, when a plastic working such as press working is performed, a plastic working material (molded body) or a partially processed material that can be uniformly deformed and has excellent dimensional accuracy can be obtained. The smaller the difference in the average crystal grain size between the surface region and the internal region, the more uniformly the plastic working is expected, so the above-mentioned ratio of the average crystal grain size: D c / D F is particularly 1 ≦ D c / A form satisfying D F ≦ 1.4 is more excellent in plastic workability. In addition, the obtained plastic working material (molded body) and the partially processed material have small variations in mechanical characteristics throughout the whole.

なお、上述のように圧延を施して、厚さが1.5mm以上である肉厚で板状のマグネシウム合金材を製造する場合、厚さ方向の全域に亘って均一的な粒径で、かつ微細な粒径とすることに限界があり、平均結晶粒径の最小値は3.5μm程度である。しかし、結晶粒径が小さいほど、塑性加工性に優れる傾向にあることから、上記板状部の平均結晶粒径も20μm以下、特に10μm以下が好ましい。平均結晶粒径は、圧延工程における圧下率や素材の加熱温度により変化し、圧下率が大きいほど、また、加熱温度が低いほど、小さくなる傾向にある。また、圧延時に塑性加工が十分に加えられ易い表面領域の平均結晶粒径は、内部領域よりも小さくなる傾向にある。   In addition, when producing a thick plate-like magnesium alloy material having a thickness of 1.5 mm or more by rolling as described above, the particle size is uniform and fine throughout the entire thickness direction. There is a limit to making the particle size small, and the minimum value of the average crystal particle size is about 3.5 μm. However, since the smaller the crystal grain size, the better the plastic workability, the average crystal grain size of the plate-like part is preferably 20 μm or less, particularly preferably 10 μm or less. The average crystal grain size varies depending on the rolling reduction in the rolling process and the heating temperature of the material, and tends to be smaller as the rolling reduction is higher and the heating temperature is lower. Further, the average crystal grain size of the surface region where plastic working is easily applied during rolling tends to be smaller than that of the internal region.

(機械的特性)
本発明マグネシウム合金材は、圧延が施されていることでダイカスト材などの鋳造材に比較して、強度や硬度、靭性などの機械的特性にも優れる上に、その厚さ方向の全域に亘って、その機械的特性を均一的に有する。例えば、上述のようにビッカース硬度が均一的な値である。表面領域と内部領域とにおいてビッカース硬度の差が小さいほど機械的弱点(低硬度部分)が実質的に存在しなくなるため、ビッカース硬度Hcの比率:Hc/HFは0.95≦Hc/HF≦1.1がより好ましい。ビッカース硬度の絶対値は、圧下率や素材の加熱温度などの圧延条件にもよるが、添加元素の含有量が多いほど、大きくなる傾向にある。なお、圧延時に塑性加工が十分に施され易い表面領域のビッカース硬度は、内部領域よりも大きくなる傾向にある。本発明マグネシウム合金材が塑性加工材(成形体)や部分加工材である場合、加工硬化により、硬度が更に高まる傾向にある。
(Mechanical properties)
The magnesium alloy material of the present invention is superior in mechanical properties such as strength, hardness, toughness and the like in the thickness direction as compared with a cast material such as a die-cast material due to rolling. And uniformly having the mechanical characteristics. For example, as described above, the Vickers hardness is a uniform value. Since the higher the mechanical weak point difference Vickers hardness is small in the surface region and the interior region (low hardness portion) is not substantially present, the ratio of the Vickers hardness H c: H c / H F is 0.95 ≦ H c / H More preferably, F ≦ 1.1. Although the absolute value of the Vickers hardness depends on rolling conditions such as the rolling reduction and the heating temperature of the material, the absolute value of Vickers hardness tends to increase as the content of the additive element increases. In addition, the Vickers hardness of the surface region where plastic working is easily performed during rolling tends to be larger than that of the internal region. When the magnesium alloy material of the present invention is a plastically processed material (molded body) or a partially processed material, the hardness tends to further increase due to work hardening.

(その他の構成)
本発明マグネシウム合金材の表面の少なくとも一部に化成処理や陽極酸化処理といった防食処理を施して防食層を具える形態とすると、耐食性により優れる。また、本発明マグネシウム合金材の表面の少なくとも一部に塗装を施して塗装層とを具える形態とすると、意匠性や商品価値を高められる。
(Other configurations)
If the anticorrosive treatment such as chemical conversion treatment or anodizing treatment is performed on at least a part of the surface of the magnesium alloy material of the present invention to provide an anticorrosion layer, the corrosion resistance is excellent. Moreover, if it is set as the form which provides a coating layer by coating at least one part of the surface of this invention magnesium alloy material, designability and commercial value can be improved.

[製造方法]
以下、上述した本発明製造方法の各工程をより詳細に説明する。
(準備工程)
<鋳造>
本発明製造方法では、出発材に連続鋳造材を利用する。連続鋳造法は、急冷凝固が可能であるため、添加元素の含有量が多い場合でも偏析や酸化物などを低減でき、割れの起点になり得る10μm超といった粗大な晶析出物の生成を抑制できる。従って、圧延などの塑性加工性に優れる鋳造材が得られる。また、連続鋳造法では、長尺な鋳造材を連続して製造可能であり、長尺材を素材に利用できる。素材が長尺である場合、長尺な圧延材を製造可能である。連続鋳造法には、双ロール法、ツインベルト法、ベルトアンドホイール法といった種々の方法があるが、板状の鋳造材の製造には、双ロール法やツインベルト法、特に双ロール法が好適であり、とりわけ特許文献1に記載の鋳造方法で製造した連続鋳造材を利用することが好ましい。鋳造材の厚さ、幅、長さは所望の圧延材(圧延板)が得られるように適宜選択することができる。鋳造材の厚さは、厚過ぎると偏析が生じ易いため、10mm以下、特に5mm以下が好ましい。得られた連続鋳造材を長尺材とする場合、円筒状に巻き取ってコイル材とすると、次工程に搬送し易い。鋳造材における巻き取り直前の箇所を100℃〜200℃程度に加熱した状態で巻き取ると、AZ91合金といった添加元素の含有量が高く、割れが生じ易い合金種であっても曲げ易くなり、巻き取り径が小さい場合でも、割れなどを生じることなく巻き取れる。得られた連続鋳造材を適宜な長さに切断したシート材を素材とすることもできる。この場合、所定の長さの圧延材(圧延板)が得られる。
[Production method]
Hereafter, each process of the manufacturing method of this invention mentioned above is demonstrated in detail.
(Preparation process)
<Casting>
In the production method of the present invention, a continuous casting material is used as a starting material. Since the continuous casting method can be rapidly solidified, segregation and oxides can be reduced even when the content of additive elements is large, and the formation of coarse crystal precipitates exceeding 10 μm that can be the starting point of cracking can be suppressed. . Therefore, a cast material excellent in plastic workability such as rolling can be obtained. In the continuous casting method, a long cast material can be continuously produced, and the long material can be used as a raw material. When the material is long, a long rolled material can be manufactured. There are various continuous casting methods such as a twin roll method, a twin belt method, and a belt-and-wheel method, but the twin roll method and the twin belt method, particularly the twin roll method are suitable for the production of a plate-shaped cast material. In particular, it is preferable to use a continuous cast material produced by the casting method described in Patent Document 1. The thickness, width, and length of the cast material can be appropriately selected so that a desired rolled material (rolled plate) can be obtained. Since the thickness of the cast material is likely to be segregated if it is too thick, it is preferably 10 mm or less, particularly preferably 5 mm or less. When making the obtained continuous cast material into a long material, if it winds up in a cylindrical shape and uses it as a coil material, it will be easy to convey to the following process. If the part immediately before winding in the cast material is rolled up in a state heated to about 100 ° C. to 200 ° C., the content of additive elements such as AZ91 alloy is high, and even if it is an alloy type that is liable to crack, it is easy to bend, Even when the take-up diameter is small, it can be wound up without causing cracks. A sheet material obtained by cutting the obtained continuous cast material into an appropriate length can be used as a raw material. In this case, a rolled material (rolled sheet) having a predetermined length is obtained.

<溶体化>
上記鋳造材に圧延を施す前に溶体化処理を施すと、鋳造材の組成を均質化したり、Alといった元素を十分に固溶させて靭性を高めたりできる。溶体化処理の条件は、例えば、加熱温度:350℃以上、特に380℃以上420℃以下、保持時間:1時間以上40時間以下が挙げられる。Mg-Al系合金である場合、Alの含有量が多いほど保持時間を長めにすることが好ましい。また、上記保持時間からの冷却工程において、水冷や衝風といった強制冷却などを利用して、冷却速度を速めると(好ましくは50℃/min以上)、粗大な析出物の析出を抑制できる。
<Solution>
When the solution treatment is performed before rolling the cast material, the composition of the cast material can be homogenized or the toughness can be enhanced by sufficiently dissolving an element such as Al. Examples of the solution treatment conditions include heating temperature: 350 ° C. or higher, particularly 380 ° C. or higher and 420 ° C. or lower, holding time: 1 hour or longer and 40 hours or shorter. In the case of an Mg—Al-based alloy, it is preferable that the holding time be longer as the Al content is higher. Further, in the cooling step from the above holding time, if the cooling rate is increased by using forced cooling such as water cooling or blast (preferably 50 ° C./min or more), precipitation of coarse precipitates can be suppressed.

<圧延>
上記鋳造材や溶体化処理材を素材とし、この素材に複数パスの圧延を施す。少なくとも1パスは、素材(鋳造材や溶体化処理材、圧延途中の加工材)を150℃以上400℃以下に加熱して行う温間圧延、或いは熱間圧延を含むことが好ましい。素材を上記温度に加熱することで、1パスあたりの圧下率を高めた場合にも圧延中に割れなどが生じ難く、上記温度を高めるほど、割れなどが少なくなり、400℃以下とすることで、素材表面の焼付きなどによる劣化や、圧延ロールの熱劣化を抑制することができる。従って、上記加熱温度は、350℃以下、更に300℃以下、特に150℃以上280℃以下が好ましい。素材だけでなく圧延ロールも加熱してもよい。圧延ロールの加熱温度は、100℃〜250℃が挙げられる。
<Rolling>
The cast material or solution treatment material is used as a raw material, and this material is subjected to multiple passes of rolling. It is preferable that at least one pass includes warm rolling or hot rolling performed by heating a raw material (a cast material, a solution treatment material, a processed material during rolling) to 150 ° C. or more and 400 ° C. or less. By heating the material to the above temperature, even when the rolling reduction per pass is increased, cracks and the like are less likely to occur during rolling, and the higher the temperature, the less the cracks, etc. Deterioration due to seizure of the material surface and thermal deterioration of the rolling roll can be suppressed. Therefore, the heating temperature is preferably 350 ° C. or lower, more preferably 300 ° C. or lower, and particularly preferably 150 ° C. or higher and 280 ° C. or lower. You may heat not only a raw material but a rolling roll. As for the heating temperature of a rolling roll, 100 to 250 degreeC is mentioned.

特に、本発明製造方法では、1パスあたりの圧下率が25%以上である圧延(以下、この圧延を強加工圧延と呼ぶ)を1パス又は複数パス行う。圧下率がこのように高い強加工圧延は、上記温間圧延、或いは熱間圧延とすることが好ましい。圧下率が高いほど、素材をその表面から内部に至って十分に塑性加工を施すことができ、均一的な組織の圧延材が得られるため、強加工圧延の圧下率は、1パスあたり30%以上が好ましく、素材に割れが生じない範囲で適宜選択することができる。強加工圧延以外の各パスの圧延(以下、この圧延を一般圧延と呼ぶ)の圧下率を10%以上とすると、素材の厚さ方向の全域に亘って均一的に、かつ十分に圧延を施すことができる。上述のように一般圧延の各パスの圧下率も高いほど、十分に塑性加工を施せるため、1パスあたり15%以上、更に20%以上とすることができる。強加工圧延・一般圧延のパス数や圧下率は、総圧下率に応じて適宜選択することができる。   In particular, in the production method of the present invention, rolling in which the rolling reduction per pass is 25% or more (hereinafter, this rolling is referred to as strong work rolling) is performed by one pass or multiple passes. The high work rolling with such a high rolling reduction is preferably the warm rolling or hot rolling. The higher the rolling reduction, the more plastic material can be processed from the surface to the inside, and a rolled material with a uniform structure can be obtained. Therefore, the rolling reduction of high work rolling is 30% or more per pass. Is preferable, and can be appropriately selected within a range in which the material does not crack. When the rolling reduction rate of each pass other than the high-strength rolling (hereinafter referred to as general rolling) is 10% or more, the rolling is performed uniformly and sufficiently over the entire thickness direction of the material. be able to. As described above, the higher the rolling reduction of each pass of general rolling, the more plastic processing can be performed, so that it can be made 15% or more, and further 20% or more per pass. The number of passes and the rolling reduction of the high work rolling / general rolling can be appropriately selected according to the total rolling reduction.

パスごとに、素材の加熱温度や圧延ロールの温度、圧下率などの条件を変更することができる。従って、各パスの圧下率は同じでもよいし、異ならせてもよい。また、パス間に中間熱処理を行ってもよい。中間熱処理を行うことで、当該熱処理までに素材に導入された歪みや残留応力などを除去・低減して、当該熱処理以降の圧延を施し易くすることができる。中間熱処理の条件は、加熱温度:150℃〜350℃(好ましくは300℃以下、より好ましくは250℃〜280℃)、保持時間:0.5時間〜3時間)が挙げられる。また、圧延後にも上記条件で最終熱処理を行ってもよい。その他、上記圧延は、潤滑剤を適宜利用すると、圧延時の摩擦抵抗を低減でき、素材の焼き付きなどを防止して、圧延を施し易い。   Conditions such as the heating temperature of the material, the temperature of the rolling roll, and the rolling reduction can be changed for each pass. Therefore, the rolling reduction rate of each pass may be the same or different. Further, intermediate heat treatment may be performed between passes. By performing the intermediate heat treatment, it is possible to remove and reduce distortions, residual stresses, and the like introduced into the material before the heat treatment, and to easily perform rolling after the heat treatment. The conditions for the intermediate heat treatment include heating temperature: 150 ° C. to 350 ° C. (preferably 300 ° C. or less, more preferably 250 ° C. to 280 ° C., holding time: 0.5 hour to 3 hours). Moreover, you may perform final heat processing on the said conditions after rolling. In addition, in the above rolling, when a lubricant is appropriately used, the frictional resistance during rolling can be reduced, and the material can be prevented from being seized and easily rolled.

その他、圧延前の鋳造材の縁部をトリミングして、圧延時、縁部に割れが存在した場合にその割れが進展しないようにしてもよいし、圧延工程の途中、圧延後などにおいて、幅を適宜調整するためにトリミングしてもよい。   In addition, the edge of the cast material before rolling may be trimmed to prevent the crack from progressing when the edge is cracked during rolling. You may trim in order to adjust suitably.

<その他の加工>
≪研磨≫
上記圧延後、研磨を施してもよい。研磨を行うことで、圧延時に使用した潤滑剤や圧延材表面に存在するキズや酸化膜などを除去、低減できる。研磨には、研削ベルトを用いると、素材が長尺材であっても、連続して容易に研磨を施せて好ましい。また、研磨は、粉末の飛散を防止するために湿式が好ましい。
<Other processing>
≪Polishing≫
You may grind | polish after the said rolling. By polishing, it is possible to remove and reduce the lubricant used during rolling, scratches and oxide films present on the surface of the rolled material, and the like. For the polishing, it is preferable to use a grinding belt because it can be easily and continuously polished even if the material is a long material. The polishing is preferably wet in order to prevent the powder from scattering.

≪矯正≫
上記圧延後や上記研磨後、矯正を施してもよい。矯正を行うことで平坦性を高められ、プレス加工などの塑性加工を精度良く行える。矯正には、複数のローラが千鳥状に配置されたロールレベラ装置を好適に利用できる。また、矯正は、例えば、素材を100℃〜300℃、特に150℃〜280℃に加熱した状態(温間矯正)で行ってもよい。
≪Correction≫
Correction may be performed after the rolling or after the polishing. By performing the correction, the flatness can be improved, and plastic processing such as press processing can be performed with high accuracy. For correction, a roll leveler device in which a plurality of rollers are arranged in a staggered manner can be suitably used. The correction may be performed, for example, in a state where the material is heated to 100 ° C. to 300 ° C., particularly 150 ° C. to 280 ° C. (warm correction).

≪塑性加工≫
上記本発明マグネシウム合金材を成形体や塑性加工部を具える部分加工材とする場合、上述した圧延工程を経た素材(上述した圧延材、研磨材、矯正材)の少なくとも一部にプレス加工といった塑性加工を施す塑性加工工程を具える製造方法により、製造することができる。この塑性加工は、200℃〜300℃の温度域で行うと、素材の塑性加工性を高められて好ましい。また、この塑性加工後に熱処理を施して、塑性加工により導入された歪みや残留応力の除去、機械的特性の向上を図ることができる。この熱処理条件は、加熱温度:100℃〜300℃、加熱時間:5分〜60分程度が挙げられる。
≪Plastic processing≫
When the magnesium alloy material of the present invention is a partially processed material having a molded body or a plastic processing portion, at least a part of the material that has undergone the rolling process described above (rolled material, abrasive material, correction material described above) and so on. It can be manufactured by a manufacturing method including a plastic processing step for performing plastic processing. This plastic working is preferably performed in a temperature range of 200 ° C. to 300 ° C., because the plastic workability of the material is improved. In addition, heat treatment can be performed after the plastic working to remove strain and residual stress introduced by the plastic working and to improve the mechanical characteristics. Examples of the heat treatment conditions include a heating temperature: 100 ° C. to 300 ° C. and a heating time: about 5 minutes to 60 minutes.

≪表面処理≫
上記本発明マグネシウム合金材を上記防食層や塗装層を具える形態とする場合、上述した圧延工程を経た素材の少なくとも一部、或いは上記塑性加工工程を経た素材の少なくとも一部に防食処理や塗装を施す表面処理工程を具える製造方法により、製造することができる。その他、上記素材の少なくとも一部に、ヘアライン加工、ダイヤカット加工、ショットブラスト加工、エッチング加工及びスピンカット加工から選択される少なくとも1種の加工を施してもよい。これらの表面処理を行うことで、耐食性や機械的保護機能を高めたり、意匠性や金属質感、商品価値を高めたりすることができる。
≪Surface treatment≫
When the magnesium alloy material of the present invention is provided with the anticorrosion layer and the coating layer, at least a part of the material that has undergone the rolling process described above, or at least a part of the material that has undergone the plastic working process, It can manufacture by the manufacturing method which comprises the surface treatment process which performs. In addition, at least one kind of processing selected from hairline processing, diamond cutting processing, shot blasting processing, etching processing, and spin cutting processing may be applied to at least a part of the material. By performing these surface treatments, corrosion resistance and mechanical protection functions can be improved, and design properties, metal texture, and commercial value can be increased.

以下、試験例を挙げて、本発明のより具体的な実施の形態を説明する。
[試験例]
以下の組成のマグネシウム合金からなる素材に、種々の条件で圧延を施して厚さ1.5mm以上のマグネシウム合金板を作製し、配向性、結晶粒径、及びビッカース硬度を調べた。
Hereinafter, more specific embodiments of the present invention will be described with reference to test examples.
[Test example]
A material composed of a magnesium alloy having the following composition was rolled under various conditions to produce a magnesium alloy plate having a thickness of 1.5 mm or more, and the orientation, crystal grain size, and Vickers hardness were examined.

この試験では、AZ91合金相当の組成を有するマグネシウム合金(Mg−8.9質量%Al−0.6質量%Zn)からなるマグネシウム合金板と、AZ31合金相当の組成を有するマグネシウム合金(Mg−3.0質量%Al−0.7質量%Zn)からなるマグネシウム合金板とを作製した。   In this test, a magnesium alloy plate made of a magnesium alloy (Mg-8.9 mass% Al-0.6 mass% Zn) having a composition equivalent to AZ91 alloy and a magnesium alloy (Mg-3.0 mass% Al--) having a composition equivalent to AZ31 alloy were used. A magnesium alloy plate made of 0.7 mass% Zn) was produced.

上記各組成のマグネシウム合金を用いて、双ロール連続鋳造法により長尺な鋳造板(厚さ4.5mm(4.50mm〜4.51mm)×幅320mm)を作製して、一旦巻き取り、鋳造コイル材を作製した。各鋳造コイル材に400℃×24時間の溶体化処理を施した。溶体化処理を施した固溶コイル材を巻き戻した素材に、表1に示す圧延条件で複数パスの圧延を施し、厚さ2.0mm(2.00mm〜2.01mm)又は1.5mm(1.50mm〜1.51mm)の圧延材(マグネシウム合金板)を作製した。各パスは温間圧延とした(素材の加熱温度:250℃〜280℃、圧延ロールの温度:100℃〜250℃)。鋳造材の厚さ、圧延途中の加工材の厚さ、得られたマグネシウム合金板の厚さはいずれも、測定対象となる板材の幅方向の中央部、及び幅方向の両縁から50mmの地点の合計3点の厚さの平均とした。   Using the magnesium alloy of each composition described above, a long cast plate (thickness 4.5 mm (4.50 mm to 4.51 mm) x width 320 mm) is produced by a twin roll continuous casting method, and once wound up, a cast coil material is obtained. Produced. Each cast coil material was subjected to a solution treatment at 400 ° C. for 24 hours. The material obtained by rewinding the solid solution coil material that has undergone solution treatment is subjected to rolling in a plurality of passes under the rolling conditions shown in Table 1, and has a thickness of 2.0 mm (2.00 mm to 2.01 mm) or 1.5 mm (1.50 mm to 1.51). mm) rolled material (magnesium alloy plate). Each pass was warm-rolled (material heating temperature: 250 ° C. to 280 ° C., roll temperature: 100 ° C. to 250 ° C.). The thickness of the cast material, the thickness of the processed material in the middle of rolling, and the thickness of the obtained magnesium alloy plate are all 50 mm from the center in the width direction of the plate to be measured and both edges in the width direction. It was set as the average of the thickness of a total of three points.

[配向性]
得られた各マグネシウム合金板についてX線回折を行い、内部領域の底面ピーク比Ocに対する表面領域の底面ピーク比OFの比率:OF/Ocを調べた。その結果を表2に示す。表面領域の底面ピーク比OFは、各マグネシウム合金板の表面に対してX線回折を行い、内部領域の底面ピーク比Ocは、各マグネシウム合金板の表面から厚さ方向に厚さの1/4までの領域(表面領域)を化学的に除去して、内部を露出させ、この露出面に対してX線回折を行った。そして、各領域の(002)面、(100)面、(101)面、(102)面、(110)面、及び(103)面のピーク強度をそれぞれ測定し、この測定結果を利用してOF/Ocを求めた。
底面ピーク比OF:IF(002)/{IF(100)+IF(002)+IF(101)+IF(102)+IF(110)+IF(103)}
底面ピーク比OC:IC(002)/{IC(100)+IC(002)+IC(101)+IC(102)+IC(110)+IC(103)}
[Orientation]
For each of the obtained magnesium alloy plate subjected to X-ray diffraction, the ratio of the bottom peak ratio O F surface area relative to the bottom surface peak ratio O c of the inner region was investigated with O F / O c. The results are shown in Table 2. Bottom peak ratio O F surface area, subjected to X-ray diffraction with respect to the surface of the magnesium alloy plate, the bottom peak ratio O c of the inner region, the first surface from the thickness in the thickness direction of the magnesium alloy plate The region up to / 4 (surface region) was chemically removed to expose the interior, and X-ray diffraction was performed on this exposed surface. And measure the peak intensity of (002) plane, (100) plane, (101) plane, (102) plane, (110) plane, and (103) plane of each region, and use this measurement result. to determine the O F / O c.
Bottom peak ratio O F: I F (002) / {I F (100) + I F (002) + I F (101) + I F (102) + I F (110) + I F (103)}
Bottom peak ratio O C : I C (002) / {I C (100) + I C (002) + I C (101) + I C (102) + I C (110) + I C (103)}

[平均結晶粒径]
得られた各マグネシウム合金板について内部領域及び表面領域の平均結晶粒径(μm)を「鋼−結晶粒度の顕微鏡試験方法 JIS G 0551(2005)」に基づいて測定した。ここでは、各マグネシウム合金板に対して厚さ方向の断面(横断面及び縦断面)をとり、各断面を光学顕微鏡で観察し(400倍)、上記各断面における表面領域(表面から厚さ方向に厚さの1/4までの領域)、及び内部領域(表面領域を除いた残部の領域)のそれぞれについて3視野ずつとり(各領域の合計視野数:6)、視野ごとに平均結晶粒径を求めた。表面領域における合計6視野の平均結晶粒径の平均値(DF)、内部領域における合計6視野の平均結晶粒径の平均値(DC)を表2に示す。また、表面領域の平均結晶粒径DFに対する内部領域の平均結晶粒径Dcの比率:Dc/DFも求めた。その結果を表2に示す。
[Average grain size]
For each of the obtained magnesium alloy plates, the average crystal grain size (μm) of the inner region and the surface region was measured based on “steel-crystal grain size microscopic test method JIS G 0551 (2005)”. Here, a cross section in the thickness direction (cross section and longitudinal section) is taken for each magnesium alloy plate, each cross section is observed with an optical microscope (400 times), and the surface region in each cross section (from the surface to the thickness direction) 3 areas (up to 1/4 of the thickness) and internal areas (remaining areas excluding the surface area), 3 fields of view (total number of fields of view: 6), average grain size for each field of view Asked. Table 2 shows the average value (D F ) of the average crystal grain size of a total of six views in the surface region and the average value (D C ) of the average crystal grain size of a total of six views in the internal region. Further, the ratio of the average crystal grain size D c in the inner region to the average crystal grain size D F in the surface region: D c / DF was also obtained. The results are shown in Table 2.

[ビッカース硬度]
得られた各マグネシウム合金板について内部領域及び表面領域のビッカース硬度(Hv)を調べた。ビッカース硬度は、平均結晶粒径の測定と同様に、各マグネシウム合金板に対して厚さ方向の断面(横断面及び縦断面)をとり、表面領域のビッカース硬度HFは、上記各断面における表面領域に圧子を押し当てて測定し、内部領域のビッカース硬度HFは、上記各断面における内部領域に圧子を押し当てて測定した。表面領域における上記両断面のビッカース硬度の平均値(HF)、内部領域における上記両断面のビッカース硬度の平均値(HC)を表2に示す。また、表面領域のビッカース硬度HFに対する内部領域のビッカース硬度Hcの比率:Hc/HFも求めた。その結果を表2に示す。
[Vickers hardness]
The Vickers hardness (Hv) of the internal region and the surface region was examined for each obtained magnesium alloy plate. Vickers hardness, as with the measurement of the average crystal grain size, taken in the thickness direction of the cross section (cross section and longitudinal section) for each magnesium alloy plates, Vickers hardness H F in the surface region, the surface of each section measured by pressing an indenter to the area, the Vickers hardness H F in the internal region was measured by pressing an indenter to the internal area of each cross section. Table 2 shows the average value (H F ) of the Vickers hardness of both cross sections in the surface region and the average value (H C ) of the Vickers hardness of both cross sections in the internal region. The ratio of the Vickers hardness H c of the inner region to the Vickers hardness H F of the surface area: H c / H F was also determined. The results are shown in Table 2.

表1,2に示すように、連続鋳造材に、1パスあたりの圧下率が25%以上の圧延を1パス以上、かつ1パスあたりの圧下率が10%以上の圧延の双方を施すことで、厚さ1.5mm以上の肉厚のマグネシウム合金板(マグネシウム合金材)であって、特定の配向性を有すると共に、その厚さ方向に均一的な組織から構成されるものが得られることが分かる。また、このマグネシウム合金板は、均一的な機械的特性を有することが分かる。   As shown in Tables 1 and 2, the continuous cast material is subjected to both rolling with a rolling reduction of 25% or more per pass and rolling with a rolling reduction of 10% or more per pass. It can be seen that a magnesium alloy plate (magnesium alloy material) having a thickness of 1.5 mm or more, having a specific orientation and having a uniform structure in the thickness direction can be obtained. . It can also be seen that this magnesium alloy plate has uniform mechanical properties.

得られた各マグネシウム合金板にプレス加工を施した。プレス加工条件は、マグネシウム合金板の加熱温度:250℃〜270℃とした。その結果、特定の配向性を有すると共に、その厚さ方向に均一的な組織から構成された試料No.A,B,D,E,G,H,J,Kは、プレス加工性に優れており、寸法精度に優れていた。また、これらの試料No.A,B,D,E,G,H,J,Kにおいて平坦な部分の組織を調べたところ、プレス加工前の各マグネシウム合金板の組織と実質的に同様であり、上記特定の配向性や平均結晶粒径を有していた。   Each magnesium alloy plate obtained was pressed. The press working conditions were a heating temperature of the magnesium alloy plate: 250 ° C. to 270 ° C. As a result, sample Nos. A, B, D, E, G, H, J, and K having a specific orientation and a uniform structure in the thickness direction are excellent in press workability. The dimensional accuracy was excellent. Further, when the structure of the flat portion was examined in these sample Nos. A, B, D, E, G, H, J, and K, it was substantially the same as the structure of each magnesium alloy plate before press working. The specific orientation and the average crystal grain size were as described above.

上記試験結果から、厚さ1.5mm以上の肉厚の板状部を有するマグネシウム合金材であって、当該板状部が特定の配向性を有する組織から構成され、かつその厚さ方向に均一的な組織から構成されることで、プレス加工性に優れることが確認された。また、プレス加工が施されたマグネシウム合金材も均一的な組織から構成されることが確認された。   From the above test results, it is a magnesium alloy material having a plate-like portion having a thickness of 1.5 mm or more, and the plate-like portion is composed of a structure having a specific orientation and is uniform in the thickness direction. It was confirmed that it was excellent in press workability by being composed of various structures. It was also confirmed that the pressed magnesium alloy material was composed of a uniform structure.

なお、上述した実施形態は、本発明の要旨を逸脱することなく、適宜変更することが可能であり、上述した構成に限定されるものではない。例えば、マグネシウム合金の組成、マグネシウム合金材の厚さ・形状、圧延工程における各パスの圧下率、パス数などを適宜変更することができる。   The above-described embodiment can be appropriately changed without departing from the gist of the present invention, and is not limited to the above-described configuration. For example, the composition of the magnesium alloy, the thickness and shape of the magnesium alloy material, the rolling reduction of each pass in the rolling process, the number of passes, and the like can be changed as appropriate.

本発明マグネシウム合金材は、自動車部品、鉄道車両部品、航空機部品、自転車部品、各種の電子・電気機器類の部品などの種々の分野の部材、及び当該部材の構成材料に好適に利用することができる。本発明マグネシウム合金材の製造方法は、上記本発明マグネシウム合金材の製造に好適に利用することができる。   The magnesium alloy material of the present invention can be suitably used for members in various fields such as automobile parts, railway vehicle parts, aircraft parts, bicycle parts, parts of various electronic and electric devices, and constituent materials of the members. it can. The manufacturing method of this invention magnesium alloy material can be utilized suitably for manufacture of the said this invention magnesium alloy material.

Claims (5)

マグネシウム合金からなり、板状部を有するマグネシウム合金材であって、
前記板状部の厚さが1.5mm以上5mm以下であり、
前記板状部は、以下の配向性を満たすことを特徴とするマグネシウム合金材。
[配向性]
前記板状部の表面から厚さ方向に厚さの1/4までの領域を表面領域、残部を内部領域とし、
前記表面領域における(002)面、(100)面、(101)面、(102)面、(110)面、及び(103)面のX線回折のピーク強度をそれぞれIF(002)、IF(100)、IF(101)、IF(102)、IF(110)、及びIF(103)とし、
前記内部領域における(002)面、(100)面、(101)面、(102)面、(110)面、及び(103)面のX線回折のピーク強度をそれぞれIC(002)、IC(100)、IC(101)、IC(102)、IC(110)、及びIC(103)とし、
前記表面領域における(002)面の配向度合い:IF(002)/{IF(100)+IF(002)+IF(101)+IF(102)+IF(110)+IF(103)}を底面ピーク比OF
前記内部領域における(002)面の配向度合い:IC(002)/{IC(100)+IC(002)+IC(101)+IC(102)+IC(110)+IC(103)}を底面ピーク比OCとするとき、
前記内部領域の底面ピーク比OCに対する前記表面領域の底面ピーク比OFの比率:OF/OCが、0.95≦OF/OC≦1.05を満たす。
A magnesium alloy material made of a magnesium alloy and having a plate-like portion,
The thickness of the plate-like portion is 1.5 mm or more and 5 mm or less ,
The said plate-shaped part satisfy | fills the following orientation, The magnesium alloy material characterized by the above-mentioned.
[Orientation]
The area from the surface of the plate-like part to 1/4 of the thickness in the thickness direction is the surface area, the remainder is the internal area,
The X-ray diffraction peak intensities of the (002) plane, (100) plane, (101) plane, (102) plane, (110) plane, and (103) plane in the surface region are I F (002), I F (100), I F (101), I F (102), I F (110), and I F (103),
The X-ray diffraction peak intensities of the (002) plane, (100) plane, (101) plane, (102) plane, (110) plane, and (103) plane in the internal region are respectively I C (002), I C (100), I C (101), I C (102), I C (110), and I C (103)
Orientation degree of (002) plane in the surface region: I F (002) / { I F (100) + I F (002) + I F (101) + I F (102) + I F (110) + I F (103)} a bottom peak ratio O F,
Orientation degree of (002) plane in the inner region: I C (002) / {I C (100) + I C (002) + I C (101) + I C (102) + I C (110) + I C (103)} when the the bottom peak ratio O C,
The ratio of the bottom peak ratio O F of the surface region relative to the bottom surface peak ratio O C of the interior region: O F / O C satisfies the 0.95 ≦ O F / O C ≦ 1.05.
前記表面領域の平均結晶粒径をDF、前記内部領域の平均結晶粒径をDcとするとき、前記表面領域の平均結晶粒径DFに対する前記内部領域の平均結晶粒径Dcの比率:Dc/DFが、2/3≦Dc/DF≦3/2を満たし、かつ、DF及びDc≧3.5μmである請求項1に記載のマグネシウム合金材。 The average crystal grain diameter D F of the surface region, when the average crystal grain size of the inner region and D c, the ratio of the average crystal grain size D c of the inner region to the average grain diameter D F of the surface area : D c / D F is, satisfies the 2/3 ≦ D c / D F ≦ 3/2, and, D F and D c ≧ 3.5 [mu] m der Ru請 Motomeko magnesium alloy material according to 1. 前記表面領域のビッカース硬度(Hv)をHF、前記内部領域のビッカース硬度(Hv)をHcとするとき、前記表面領域のビッカース硬度HFに対する前記内部領域のビッカース硬度Hcの比率:Hc/HFが、0.85≦Hc/HF≦1.2を満たす請求項1又は請求項2に記載のマグネシウム合金材。 Vickers hardness (Hv) H F of the surface region, wherein the Vickers hardness of the inner region (Hv) when the H c, the ratio of the Vickers hardness H c of the inner region with respect to the Vickers hardness H F of the surface area: H c / H F is, 0.85 ≦ H c / H F ≦ 1.2 and less than to請 Motomeko 1 or a magnesium alloy material according to claim 2. 前記マグネシウム合金は、添加元素にAlを5.0質量%以上12質量%以下含有する請求項1〜請求項3のいずれか1項に記載のマグネシウム合金材。 Wherein said magnesium alloy, the additive element you containing Al 5.0 mass% or more and 12 mass% or less Motomeko 1 magnesium alloy material according to any one of claims 3. マグネシウム合金からなる素材に圧延を施してマグネシウム合金材を製造するマグネシウム合金材の製造方法であって、
溶解したマグネシウム合金を双ロール鋳造法により連続鋳造した厚さ10mm以下の板状の素材を準備する準備工程と、
前記素材に複数パスの圧延を施して、厚さ1.5mm以上5mm以下の板状のマグネシウム合金材を製造する圧延工程とを具え、
前記準備工程では、前記素材として、連続鋳造材に350℃以上420℃以下の溶体化処理を施したものを準備し、
前記圧延工程では、圧延時の素材の温度を150℃以上280℃以下とし、圧延ロールの温度を100℃以上250℃以下とし、1パスあたりの圧下率が25%以上の圧延を少なくとも1パス行い、残りの各パスの圧下率を10%以上とするマグネシウム合金材の製造方法。
A method for producing a magnesium alloy material by rolling a material made of a magnesium alloy to produce a magnesium alloy material,
A preparation step of preparing a plate-like material having a thickness of 10 mm or less continuously cast by a twin-roll casting method of a melted magnesium alloy;
A rolling process for producing a plate-like magnesium alloy material having a thickness of 1.5 mm or more and 5 mm or less by performing a plurality of passes of rolling on the material,
In the preparation step, as the raw material, a continuous cast material is subjected to a solution treatment at 350 ° C. or higher and 420 ° C. or lower,
In the rolling step, the temperature of the material during rolling is set to 150 ° C. or higher and 280 ° C. or lower, the temperature of the rolling roll is set to 100 ° C. or higher and 250 ° C. or lower, and rolling at a rolling reduction rate of 25% or higher per pass is performed at least one pass. the rest of the manufacturing method of each path at a reduction ratio of 10% or more to luma magnesium alloy material.
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